Toward Single Atom Chains with Exfoliated Tellurium
© The Author(s). 2017
Received: 15 June 2017
Accepted: 27 July 2017
Published: 10 August 2017
We demonstrate that the atom chain structure of Te allows it to be exfoliated as ultra-thin flakes and nanowires. Atomic force microscopy of exfoliated Te shows that thicknesses of 1–2 nm and widths below 100 nm can be exfoliated with this method. The Raman modes of exfoliated Te match those of bulk Te, with a slight shift (4 cm−1) due to a hardening of the A1 and E modes. Polarized Raman spectroscopy is used to determine the crystal orientation of exfoliated Te flakes. These experiments establish exfoliation as a route to achieve nanoscale trigonal Te while also demonstrating the potential for fabrication of single atom chains of Te.
KeywordsAtom chain Tellurium Exfoliation 1D layered material
Dominated by carbon nanotubes and semiconductor nanowires, one dimensional (1D) materials have been extensively investigated for their extraordinary properties for electronics, photonics, and optoelectronics [1, 2]. Opportunities provided by 1D materials include transistors scaled to the smallest possible dimensions [3, 4], extremely sensitive chemical and biological sensors [5, 6], and unique electronic phenomena originating from the similarity of optical fibers and ballistic electrons inside a 1D wire [7, 8]. Progress with carbon nanotubes for most applications has been hampered by chirality randomness, and at the smallest diameters, semiconductor nanowire properties are degraded by surface dangling bonds. Consequently, the focus of low-dimensional material research has shifted primarily to two-dimensional (2D) layered materials, which combine atomic-scale thickness and high-performance physical properties by virtue of weak bonding in one direction [9–13].
The layered material concept may be generalized from 2D materials, with weak bonds in one direction, to 1D materials, with weak bonds in two directions. Many 1D weakly bonded solids are now known [14, 15]. One-dimensional weakly bonded materials may be separated to produce small diameter nanowires, as has been done with Li2Mo6Se6 [16, 17]. We argue that 1D weakly bonded materials present an opportunity to revisit 1D materials, with a new possibility to achieve single atom chains with atomic-scale diameters and an expectation of new physical properties stemming from crystal structures that are distinct from both carbon nanotubes and semiconductor nanowires. The anisotropic structure of 1D weakly bonded materials may allow single atom chains to be created by exfoliation, or possibly directly grown by molecular beam epitaxy or chemical vapor deposition.
They are predicted to have direct semiconducting band gaps of 1 and 2 eV for Te and Se, respectively, with strongly thickness-dependent band gaps , creating new opportunities for tiny, wavelength-tunable detectors and emitters.
The helical structure of Se and Te chains is expected to confer unique electrical, optical, and mechanical properties, including novel spin-orbit coupling effects boosted by heavy Se and Te atoms , negative compressibility and band gap narrowing under pressure and strain , and extraordinary flexibility greater than typical elastic polymers .
Since they are composed of a single element, an isolated Se or Te atom chain would have the smallest diameter of any known 1D material. The height of the triangular spiral cross-section is 2 Å, and the inter-chain distance is 3.4 Å .
Experimental demonstration of the atom chain concept originates with STM manipulation of individual atoms on a substrate to achieve linear and planar arrays of coupled atoms [24, 25]. In addition to atom-by-atom assembly on surfaces, step edges of substrates have been decorated with atom chains , and self-assembled growth has been used to create large-area arrays of atom chains . However, depending on the approach, all these pioneering experiments do not allow 1D structures to be created over large scales, choice of materials is limited, or the structure is strongly bound to the substrate. In principle atom chains derived from 1D weakly bonded materials could overcome these limitations.
To date, the anisotropic structure of Se and Te has permitted growth of small diameter nanowires [28, 29], self-assembly of single chains inside zeolite pores [30, 31] and carbon nanotubes , the growth of 2D monolayer trigonal Te on graphene , and solution-growth of 2D Te [34, 35]. This earlier work demonstrates the tendency of Te to form chains and nanowires that are relatively stable mechanically and chemically outside the bulk Te crystal structure. Our objective is to use exfoliation of solid Te as a route to obtain single atom chains.
Results and Discussion
Tellurium was exfoliated in anisotropic linear bands with lengths up to 50 μm (Fig. 2a). Atomic force microscopy of some of these bands reveals heights in the 10–15 nm range (Fig. 2c), with ridges running along the length of the bands that are evident in both the height image and a height profile taken perpendicular to one of the bands as shown in Fig. 2d. The modulated surface pattern and variation in wire width are evidence that the atom chains randomly break away from the bulk crystal both laterally and vertically, unlike 2D layered materials such as graphene which exfoliate with mostly flat surfaces whether a tape or sliding technique is used. We were able to obtain wires of 1–2 nm thickness using this sliding technique.
Stability in ambient environment is a concern for any newly exfoliated material because surface reactions that are negligible in bulk materials can dominate the properties of ultrathin exfoliated materials. An optical image of the same Te sample in Fig. 2a is shown in Fig. 2b after storage for 3 weeks in air. Aside from differences in color contrast due to camera settings, the aged sample appears virtually the same as when it was freshly exfoliated. In particular, we note a complete absence of the blistering that occurs when 2D black phosphorus degrades in air . This observation is consistent with the observation that the timescale for degradation of Te nanowires in various solvents such as water is not indefinite but quite long, from hours to days .
The Raman spectrum of an approximately 30-nm-thick Te flake (red circle in Fig. 3a) shows the same two peaks, shifted to slightly higher frequencies (Fig. 4a). The measured Raman peak of the silicon substrate at 520.9 cm−1 (not shown) indicates that the spectrometer is calibrated to better than 1 cm−1. We also note that the exfoliated Te spectrum shown in Fig. 4a, which was measured in air several weeks after exfoliation, is not consistent with the Raman spectra of either amorphous  or oxidized Te , which also establishes the environmental stability of ultrathin exfoliated Te. Despite a slight asymmetry in the Raman peaks for both bulk and exfoliated Te, a pair of Lorentzians fits the spectra reasonably well (black curves in Fig. 4a). Peak parameters extracted from the fits indicate a mode hardening for the exfoliated flake relative to the bulk crystal of 4 cm−1 for the A1 mode and 2 cm−1 for the E mode.
One interpretation of this mode hardening is a flake-substrate interaction, for example, if the Te is strained as it is exfoliated on the SiO2 substrate. Interaction with the substrate also generically hardens the radial breathing modes of carbon nanotubes . Another possibility is that inter-chain interactions are reduced in ultrathin Te because a significant fraction of chains is missing one or more neighbors. A naïve expectation would be that weaker inter-chain coupling would soften the A1 mode; however, applying pressure to Te crystals is known to reduce the A1 frequency . Further, the A1 frequency of isolated Te chains inside zeolite nanopores, where inter-chain coupling is zero (or significantly less than for bulk, considering the 6.6 Å nanopore diameter), is much higher than in bulk Te at 172 cm−1 . The observation that reduced inter-chain coupling hardens Te Raman modes is explained by a competition between inter- and intra-chain forces in Ref. . Our measurement of a smaller shift for the E mode than the A1 mode (Fig. 4a) is also consistent with the pressure dependence reported in Ref. , but substrate-induced strain may be expected to produce similar behavior. We are unable to conclude within the scope of this work whether substrate interaction or reduced inter-chain interactions are responsible for the spectral shifts we observe.
For the sample shown in Fig. 3, both optical and atomic force microscopy display elongated, horizontally aligned Te flakes, which suggests that the c-axis of the Te crystal is horizontal in these images. However, the AFM images (Fig. 3b, c) also show that a significant fraction of the exfoliated flakes, particularly the thinnest ones, are tilted 45° away from horizontal. To confirm the crystal orientation of this sample, we use polarization-resolved Raman spectroscopy. The polarization of the excitation beam was rotated with a half-wave plate, and the integrated Raman intensity from 85 to 170 cm−1 is shown in Fig. 4b. The intensities were normalized by the laser power under the microscope objective measured at each polarization angle. The Raman intensity shows two maxima within one full rotation, located at 45° and 225° with respect to the X and Y axes defined in the microscope images (Fig. 3). The intensity varies approximately sinusoidal (black curve in Fig. 4b), with an amplitude of +/−15% over a constant background.
Meanwhile, the optical absorption of bulk Te at 633 nm is stronger for light polarized perpendicular to the c-axis than for parallel polarization . For Te flakes with nearly bulk-like optical properties (Fig. 4a), we therefore expect Raman intensity to be higher for light polarized perpendicular to the c-axis. Based on the angle of the Raman maximum in Fig. 4b, we conclude that the Te nanowires oriented at 45° in Fig. 3b, c are elongated parallel to the c-axis for that sample. Because different Te flakes on the same substrate were used for Raman spectroscopy and AFM, an assumption of this conclusion is that the crystal axes are the same for all exfoliated flakes shown in Fig. 3a. This assumption would not be appropriate for flakes prepared by the traditional tape exfoliation method, but it is a reasonable assumption for the unidirectional rubbing technique used here. These observations demonstrate that polarized Raman spectroscopy is sufficient to determine the crystal orientation of nanoscale exfoliated Te. This technique is useful in practice given that optical and atomic force microscopy do not provide unambiguous information about crystal orientation. As the thickness and width of exfoliated Te approaches the single atom chain limit, we expect a cross-over in the crystal direction associated with maximum Raman scattering because isolated Te chains inside nanopores have maximum Raman intensity for polarization parallel to the c-axis .
We have introduced trigonal Te as a weakly bonded material capable of being exfoliated to produce ultrathin Te single crystals. We demonstrate that the atom chain structure of Te allows it to be exfoliated as two-dimensional flakes and one-dimensional nanowires. Atomic force microscopy of exfoliated Te shows that thicknesses of 1–2 nm and wires of about 100 nm width can be exfoliated with this method. The Raman modes of exfoliated Te match those of bulk Te, with a slight shift (4 cm−1) due to a hardening of the A1 and E modes. Polarized Raman spectroscopy is used to determine the crystal orientation of exfoliated Te flakes. These experiments establish exfoliation as a route to achieve nanoscale trigonal Te while demonstrating the potential for fabrication of single atom chains of Te. Our current efforts are focused on producing Te or Se single atom chains by molecular beam epitaxy or by improving exfoliation.
We acknowledge J. M. grant for graphical assistance. This work was supported by AFOSR award numbers FA9550-14-1-0205 (S.-Q.Y.) and FA9550-16-1-0203 (H.C.). H. C. acknowledges support from the University of Arkansas Connor Faculty Fellowship.
Availability of Data and Materials
The corresponding author (HC) should be contacted regarding requests for data and materials.
HC, GS, and SQY conceived of the experiment and directed the research. IS grew the Te single crystals. HC and TH produced exfoliated Te samples. HC, TH, XH, and JS and acquired the data. HC, TH, and GS analyzed the data. HC, GS, and SQY wrote the manuscript with input from all authors. All authors read and approved the final manuscript.
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- Jorio A, Dresselhaus G, Dresseldhaus MS, editors (2008) Carbon nanotubes. Springer, New YorkGoogle Scholar
- Zhang A, Zheng G, Lieber CM (2016) Nanowires. Springer, SwitzerlandGoogle Scholar
- Tans SJ, Verschueren ARM, Dekker C (1998) Room-temperature transistor based on a single carbon nanotube. Nature 393:49Google Scholar
- Cui Y, Duan X, Hu J, Lieber CM (2000) Doping and electrical transport in silicon nanowires. J Phys Chem B 104:5213Google Scholar
- Kong J et al (2000) Nanotube molecular wires as chemical sensors. Science 287:622Google Scholar
- Cui Y, Wei Q, Park H, Lieber CM (2001) Nanowire nanosensors for highly sensitive and selective detection of biological and chemical species. Science 293:1289Google Scholar
- Liang W et al (2001) Fabry - Perot interference in a nanotube electron waveguide. Nature 411:665Google Scholar
- Refael G, Heo J, Bockrath M (2007) Sagnac interference in carbon nanotube loops. Phys Rev Lett 98:246803Google Scholar
- Novoselov KS et al (2004) Electric field effect in atomically thin carbon films. Science 306:666Google Scholar
- Novoselov KS et al (2005) Two-dimensional gas of massless Dirac fermions in graphene. Nature 438:197Google Scholar
- Zhang Y, Tan Y-W, Stormer HL, Kim P (2005) Experimental observation of the quantum Hall effect and Berry's phase in graphene. Nature 438:201Google Scholar
- Novoselov KS et al (2005) Two-dimensional atomic crystals. Proc Nat Acad Sci USA 102:10451Google Scholar
- Avouris P, Heinz TF, Low, T (2017) 2D materials: properties and devices. Cambridge, New YorkGoogle Scholar
- Cheon G et al (2017) Data mining for new two- and one-dimensional weakly bonded solids and lattice-commensurate heterostructures. Nano Lett 17:1915Google Scholar
- Island JO et al (2017) Electronics and optoelectronics of quasi-one dimensional layered transition metal trichalcogenides. https://arxiv.org/abs/1702.01865 Google Scholar
- Venkataraman L, Lieber CM (1999) Molybdenum selenide molecular wires as one-dimensional conductors. Phys Rev Lett 83:5334Google Scholar
- Venkataraman L, Kim P (2006) Electron transport in a multichannel one-dimensional conductor: molybdenum selenide nanowires. Phys Rev Lett 96:076601Google Scholar
- Hippel ARvon (1948) Structure and conductivity in the VIb group of the periodic system. J Chem Phys 16:372Google Scholar
- Joannopoulos JD, Schlüter M, Cohen ML (1975) Electronic structure of trigonal and amorphous Se and Te. Phys Rev B 11:2186Google Scholar
- Entin MV, Magarill LI (2002) Electrons in a twisted quantum wire. Phys Rev B 66:205308Google Scholar
- Ren W, Ye J-T, Shi W, Tang Z-K, Chan CT, Sheng P (2009) Negative compressibility of selenium chains confined in the channels of AlPO4-5 single crystals. New J Phys 11:103014Google Scholar
- Flory PJ (1969) Statistical mechanics of chain molecules. Interscience, New YorkGoogle Scholar
- Martin RM, Lucovsky G, Helliwell K (1976) Intermolecular bonding and lattice dynamics of Se and Te. Phys Rev B 13:1383Google Scholar
- Eigler DM, Schweizer EK (1990) Positioning single atoms with a scanning tunnelling microscope. Nature 344:524Google Scholar
- Yazdani A, Eigler DM, Lang ND (1996) Off-resonance conduction through atomic wires. Science 272:1921Google Scholar
- Gambardella P et al (2002) Ferromagnetism in one-dimensional monatomic metal chains. Nature 416:301Google Scholar
- Yeom HW et al (1999) Instability and charge density wave of metallic quantum chains on a silicon surface. Phys Rev Lett 82:4898Google Scholar
- Qian HS et al (2006) High-quality luminescent tellurium nanowires of several nanometers in diameter and high aspect ratio synthesized by a poly (vinyl pyrrolidone)-assisted hydrothermal process. Langmuir 22:3830Google Scholar
- Xi G et al (2006) Large-scale synthesis, growth mechanism, and photoluminescence of ultrathin Te nanowires. Cryst Growth Des 6:2567Google Scholar
- Bogomolov VN (1978) Liquids in ultrathin channels (Filament and cluster crystals). Sov Phys Usp 21:77Google Scholar
- Li IL et al (2005) Resonant Raman study of confined Se single helix and Se8 rings. Appl Phys Lett 87:071902Google Scholar
- Medeiros PVC et al (2017) Extreme Te nanowires encapsulated within ultra-narrow single-walled carbon nanotubes. https://arxiv.org/abs/1701.04774 Google Scholar
- Huang X et al (2017) Epitaxial growth and band structure of Te film on graphene. https://arxiv.org/abs/1703.07062 Google Scholar
- Wang Y et al (2017) Large-area solution-grown 2D tellurene for air-stable, high-performance field-effect transistors. https://arxiv.org/abs/1704.06202 Google Scholar
- Du Y et al (2017) 1D van der Waals material tellurium: Raman spectroscopy under strain and magneto-transport. https://arxiv.org/abs/1704.07020 Google Scholar
- Shih I, Champness CH (1978) Czochralski growth of tellurium single crystals. J Cryst Growth 44:492Google Scholar
- Navarro-Moratalla E et al (2016) Enhanced superconductivity in atomically thin TaS2. Nat Comm 7:11043Google Scholar
- Wood JD et al (2014) Effective passivation of exfoliated black phosphorus transistors against ambient degradation. Nano Lett 14:6964Google Scholar
- Lan W-J et al (2007) Dispersibility, stabilization, and chemical stability of ultrathin tellurium nanowires in acetone: morphology change, crystallization, and transformation into TeO2 in different solvents. Langmuir 23:3409Google Scholar
- Pine AS, Dresselhaus G (1971) Raman spectra and lattice dynamics of tellurium. Phys Rev B 4:356Google Scholar
- Lucovsky G (1967) The structure of amorphous selenium from infrared measurements. In: Cooper WC, editor. The physics of selenium and tellurium. Canada. P. 255–267Google Scholar
- Oyobuturi TS (1971) Physical properties of tellurium. J Soc Appl Phys 40:594Google Scholar
- Richter WJ (1972) Extraordinary phonon Raman scattering and resonance enhancement in tellurium. Phys Chem Solids 33:2123Google Scholar
- Brodsky MH et al (1972) The Raman spectrum of amorphous tellurium. Phys Stat Sol B 52:609Google Scholar
- Mirgorodsky AP et al (2000) Dynamics and structure of TeO2 polymorphs: model treatment of paratellurite and tellurite; Raman scattering evidence for new γ- and δ-phases. J Phys Chem Solids 61:501Google Scholar
- Araujo PT et al (2010) Resonance Raman spectroscopy of the radial breathing modes in carbon nanotubes. Physica E 42:1251Google Scholar
- Richter W et al (1973) Hydrostatic pressure dependence of first-order Raman frequencies in Se and Te. Phys Stat Sol B 56:223Google Scholar
- Poborchii VV (1996) Polarized Raman and optical absorption spectra of the mordenite single crystals containing sulfur, selenium, or tellurium in the one-dimensional nanochannels. Chem Phys Lett 251:230Google Scholar
- Stuke J, Keller H (1964) Optical properties and band structure in the system Se-Te. Phys Status Solidi 7:189Google Scholar