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Article

Temperature-Dependent Raman Scattering of Large Size Hexagonal Bi2Se3 Single-Crystal Nanoplates

by
Fang Zhou
1,2,3,
Yujing Zhao
2,
Weichang Zhou
1 and
Dongsheng Tang
1,*
1
Synergetic Innovation Center for Quantum Effects and Application, Key Laboratory of Low-Dimensional Quantum Structures and Quantum Control of Ministry of Education, School of Physics and Electronics, Hunan Normal University, Changsha 410081, China
2
College of Mechanical engineering and Photoelectric Physics, Hunan Engineering Laboratory for Preparation Technology of Polyvinyl Alcohol Fiber Material, Huaihua University, Huaihua 418008, China
3
Department of Basic Course, Hunan Police Academy, Changsha 410138, China
*
Author to whom correspondence should be addressed.
Appl. Sci. 2018, 8(10), 1794; https://doi.org/10.3390/app8101794
Submission received: 19 August 2018 / Revised: 17 September 2018 / Accepted: 26 September 2018 / Published: 1 October 2018
(This article belongs to the Section Nanotechnology and Applied Nanosciences)
Browse Figures
Versions Notes

Abstract

:
Bi 2 Se 3 has extensive application as thermoelectric materials. Here, large-scale Bi 2 Se 3 single-crystal hexagonal nanoplates with size 7.50–10.0 μ m were synthesized successfully by hydrothermal method. X-ray diffraction (XRD), scanning electron microscope (SEM), and transmission electron microscope (TEM) were used to characterize the Bi 2 Se 3 nanoplates, which confirm the single-crystal quality and smooth surface morphology with large size. Micro-Raman spectra over a temperature range of 83–603 K were furthermore used to investigate the lattice dynamics of Bi 2 Se 3 nanoplates. Both 2A g 1 and 1E g 2 modes shift evidently with reduced temperature. The line shape demonstrates a significant broadening of full width at half maximum (FWHM) and red-shift of frequency with increased temperature. The temperature coefficient of A 1 g 1 , E g 2 , A 1 g 2 modes were determined to be −1.258 × 10 − 2 cm − 1 /K, −1.385 × 10 − 2 cm − 1 /K, −2.363 × 10 − 2 cm − 1 /K, respectively. Such low temperature coefficient may favor the obtaining of a high figure of merit (ZT) and indicate that Bi 2 Se 3 nanoplates were used as excellent candidates of thermoelectric materials.

1. Introduction

Recently, 3D layered topological insulators (TIs) materials, such as Bi 2 Se 3 , Bi 2 Te 3 , and Sb 2 Te 3 , have attracted extensive attention due to their unique surface state properties, which are topologically protected against back-scattering and immune to defect-driven localization [1,2,3]. These materials also are fascinating materials conventionally used in thermoelectricity [4,5]. Thermoelectric materials can be used to directly convert waste heat into electrical power, which is a potential technology for clean and reliable energy harvesting [6]. Improving the energy conversion efficiency is the ultimate goal of global researchers. The record of conversion efficiency was refurbished continuously in the past decade [7,8]. The thermoelectric efficiency is governed by the dimensionless thermoelectric figure of merit ZT (ZT = S 2 σ T/K, where S, σ , T, and K denote the Seebeck coefficient, electrical conductivity, absolute temperature, and thermal conductivity, respectively) [9]. Nanostructuring to minimize the thermal conductivity is one of the most common approaches to obtain high ZT [10,11]. For example, nanostructured lead chalcogenides PbQ (Q = Te, Se, S) have demonstrated high thermoelectric ZT [12]. However, Pb-free materials are more desirable to replace the toxic PbQ, which may be unfriendly to the environment and human health.
Raman spectroscopy is a conventional and non-destructive technique for crystal structure characterization [13], which can provide important information on lattice vibration, doping, strain engineering, and crystal phases [14,15]. Insight into the lattice dynamics property is essential to understand the thermal/transport properties, thermal expansion and diffusion, entropy, specific heat, and electron-phonon interaction, all of which have great impact on the thermoelectric performance [16]. Furthermore, it is well known that change of temperature can vary inter-atomic distances and vary the overlap among adjacent electronic orbitals. Therefore, temperature-dependent Raman spectra are well suitable to obtain information on the thermal conductivity of materials, as well as isotopic effects and phonon lifetimes [17,18,19].
With a band gap of 0.3 eV, Bi 2 Se 3 is the most important V–VI semiconductor [20,21,22,23]. Bi 2 Se 3 has an extensive application as thermoelectric and photoelectric materials near the room temperature [24,25]. Raman spectroscopy was an important tool to characterize the physical properties of various nanostructures, such as: 1T-TaS 2 [26], TiS 3 [27], MoS 2 [28], CoFe 2 O 4 [29], CuGaO 2 [30], Bi 3 . 25 La 0.75 Ti 3 O 12 [31], ZnSe [18,32], ZnO [33], etc. Recently, there are some reports about the Raman-active optical phonon of Bi 2 Se 3 micro/nanostructures [34,35,36]. For example, Zhang et al. reported the synthesis and Raman spectra investigation of few-quintuple layer Bi 2 Se 3 nanoplates [37]. However, the size of their Bi 2 Se 3 nanoplates was only 0.7–1.6 μ m, which makes it hard to obtain the Raman spectra of a single nanoplate under optical microscopy. Therefore, it is highly desired to synthesize large Bi 2 Se 3 nanoplates with only a few layers in thickness. As far as we know, there is not yet any report on the Raman spectra of the single solution process Bi 2 Se 3 nanoplate. Herein, we synthesized large (7.50–10.0 μ m) Bi 2 Se 3 hexagonal single-crystal nanoplates by hydrothermal method and investigated their Raman spectra over a wide temperature range of 83–603 K. The variation of Raman peak position and full wave at half maximum (FWHM) with temperature were discussed in detail. The temperature coefficient of A 1 g 1 , E g 2 , A 1 g 2 modes were determined to be −1.258 × 10 − 2 cm − 1 /K, −1.385 × 10 − 2 cm − 1 /K, −2.363 × 10 − 2 cm − 1 /K, respectively. Our results demonstrate that Bi 2 Se 3 nanoplates might act as excellent candidates of thermoelectric materials.

2. Experimental Sections

2.1. Preparation of Bi 2 Se 3 Nanoplates

All of the reagents used in the experiment were of analytical purity and used without further purification. The typical synthesis procedure is as follows. First, 6 mmol SeO 2 , 2 mmol Bi 2 O 3 , 0.8 g NaOH were dissolved in ethylene glycol (EG). Second, this solution was transferred into a Teflon autoclave, which was heated at 180 ∘ C for 7 h and then cooled to room temperature. The precipitates were centrifuged, washed with distilled water, acetone, and absolute ethanol for several times, and finally dried at 60 ∘ C for 6 h.

2.2. Sample Characterization

Phase identification and structure analysis of the as-obtained sample were carried out by X-ray powder diffraction (XRD, Bruker D8 Advance). The morphology of the final product was characterized by scanning electron microscope (SEM, FEI, NovaSEM-450). The chemical composition and elemental mapping of the sample were analyzed by energy—dispersive X-ray (EDX) spectroscopy. Transmission electron microscope (TEM), high-resolution TEM (HRTEM), and selected area electron diffraction (SAED) pattern were characterized by TEM (FEI, Tecnai F 20) operating at 200 kV. Raman spectra were measured by high-resolution Raman spectrometer (LabRAM HR Evolution, Horiba JY) using continuous wave (CW) laser with wavelength of 514.5 nm (5 mW excitation power) as excitation light source. The different temperatures were obtained by using Limkam THMS600.

3. Results and Discussion

3.1. Structure and Morphology of Bi 2 Se 3 Nanoplates

Figure 1 is the XRD pattern of as-prepared Bi 2 Se 3 nanostructures. All the diffraction peaks in the XRD pattern match well with the Bi 2 Se 3 rhombohedral lattice phase (JCPDS: 89-2008), and the estimated lattice constants are a = 0.42 nm and c = 2.87 nm. The six main peaks can be easily indexed to (015), (1,0,10), (1,0,15), (205), (0,2,10) and (1,1,15) planes of Bi 2 Se 3 rhombohedral lattice phase [38,39].
Figure 2a is SEM image of Bi 2 Se 3 nanoplates, which shows the uniform hexagonal morphology in large scale. Figure 2b is low magnification TEM image of single Bi 2 Se 3 nanoplate, which has a typical flat surface and sharp edges. These Bi 2 Se 3 nanoplates have size of 7.50–10.0 μ m, which is large enough to be observed in the optical microscopy for Raman measurement. The SAED pattern shown in Figure 2c exhibits a hexagonal symmetry diffraction spot pattern and indicates the single-crystal nature of Bi 2 Se 3 nanoplates. Figure 2d is high-resolution TEM (HRTEM) image [40,41]. The plane spacings were measured to be 0.35 nm. Raman spectrum of single Bi 2 Se 3 nanoplate at room temperature is shown in Figure 2e. Three Raman optical phonon modes can be identified as A 1 g 1 at 68 cm − 1 , E g 2 at 127 cm − 1 , and A 1 g 2 at 170 cm − 1 . The peak positions are consistent with the previously measured bulk crystalline Bi 2 Se 3 [41].
Hydrothermal method is the chemical reaction in solution at low temperature (below 250 ∘ C). It is a simple while powerful method to obtain desirable crystal materials. By using the hydrothermal method, various structures, include 3D bulk materials, 2D nanoplates, 1D nanowires and 0D nanoparticles, can be synthesized controllable no whether their layer or non-layer nature. The present data indicates that the crystallinity of hydrothermal synthesized Bi 2 Se 3 was compared to that of Bridgman method, which was known for the fabrication of single crystal with high crystal quality. Compared with ref 36, we reported the Bi 2 Se 3 nanoplates with large size and uniform morphology, which may be used as integrated chip and have potential application in photonics and electronics nanodevices, and our results were based on the single nanoplate that ensured the accurate Raman shift and lattice dynamics.

3.2. Temperature-Dependent Raman Spectroscopy

The rhombohedral crystal structure of Bi 2 Se 3 belongs to the D 3 d 5 (R 3 ¯ m) space group symmetry. There are five atoms per unit cell in the Bi 2 Se 3 . This compound contains sandwich structure of the five layers [Se(1)-Bi-Se(2)-Bi-Se(1)], which are held together by van der Waals force. According to the group theory, there are 12 optical modes in Bi 2 Se 3 . However, four modes (2A u 1 and 2E u ) are infrared active and can not be observed in the Raman spectrum. So, only eight modes were explained [36,40]. The irreducible representation for the zone-center phonons can be written as [42]:
Γ = 2 E g + 2 A 1 g + 2 E u + 2 A 1 u
It must be noted that the thickness-dependent vibrational frequency of E g 1 mode is mainly due to the weak van der Waals interlayer interaction. Similar with graphene and MoS 2 [43,44], this mode completely vanishes under single-layer limitation. Here, a, b, and c is a crystal lattice constant of Bi 2 Se 3 , respectively. The Raman tensor of Bi 2 Se 3 are expressed as: [45]
A g = a 0 0 0 a 0 0 0 a , E g = c 0 0 0 − c d d 0 0 , 0 − c d − c 0 0 d 0 0 ,
For temperature-dependent Raman scattering, the Raman spectra were collected by varying the temperature in the range of 83–603 K. As shown in Figure 3a, the intensities of Raman peaks increase significantly with decreased temperature. When the temperature increased from 83 to 603 K, A 1 g 1 , E g 2 , and A 1 g 2 modes are observed to follow a monotonous shift to low wavenumber direction. Such as: the frequency of A 1 g 1 mode moved from 72 cm − 1 to 64 cm − 1 (Figure 3b). The frequency of E g 2 mode moved from 130 cm − 1 to 123 cm − 1 (Figure 3c). The frequency of A 1 g 2 mode moved from 174 cm − 1 to 163 cm − 1 (Figure 3d). We analyzed and discussed the red-shift of Raman peaks and temperature coefficients in Figure 3 and Figure 4. Generally, the research of temperature-dependent Raman spectroscopy is an efficient way to investigate the thermal expansion, thermal conductivity, and interlayer coupling [46,47]. In our experiment, all the Raman peaks had an obvious red-shift with the temperature increasing from 80 to 603 K. In addition, the peak shifts had a linear dependence with the temperature, yielding the first-order temperature coefficient ( χ ). It has been proposed that the temperature-dependent peak positions in Raman spectroscopy may result from anharmonicity that results from the thermal expansion and contraction of the crystal and phonon modes [48]. The temperature-dependent line width and intensity could be attributed to the zone-center optical phonon decaying into an optical phonon and an acoustic phonon [48,49,50].
Figure 4a–d plot the peak frequency and FWHM of A 1 g 1 , E g 2 , and A 1 g 2 modes from 83 to 603 K in detail to investigation the temperature effect. The FWHM increased with increase temperature. The peak frequency and FWHM of phonon modes at each temperature can be predicted by theoretical Raman line shape, which can be written as [51]:
I ( ω ) = χ 0 Γ 0 ω ω 0 2 ( n ˜ + 1 ) ( ω 0 2 − ω 2 ) 2 + ω 2 Γ 0 2 ,
where n ˜ = e x p [ ℏ χ κ B T ] − 1 is the phonon occupation number, ω 0 and Γ 0 are the peak position and the line width, χ 0 is related with peak intensity, respectively. The peak position and FWHM of these phonon modes at each temperature in our results are consistent with theoretical Raman line shape. The relationship between the peak frequency and temperature was written as [52]:
ω ( T ) = ω 0 + χ T ,
where ω 0 is the frequency of vibration of these phonon modes at absolute zero temperature, χ is the first-order temperature coefficient of these phonon modes. The evolution of the Raman peak position, ω , follows a linear dependence with the temperature. The different Raman modes χ i of the first-order temperature coefficients can be fitted linearly. The values of temperature coefficient for each Raman mode are listed in Table 1.
Figure 4 and Table 1 indicate the temperature evolution for the three Raman modes A 1 g 1 , E g 2 , A 1 g 2 , measured on the Bi 2 Se 3 hexagonal single-crystal nanoplates sample. For the Bi 2 Se 3 nanoplates, the first order temperature coefficients are χ 1 = −1.258 × 10 − 2 cm − 1 /K, χ 2 = −1.385 × 10 − 2 cm − 1 /K, χ 3 = −2.363 × 10 − 2 cm − 1 /K.
Bi 2 Se 3 , a typical thermoelectric material, has temperature evolution of Raman mode further relative to other two-dimensional materials, such as, the transition metal dichalcogenides (TMDCs) (MoS 2 , MoSe 2 , WS 2 , and WSe 2 ), black phosphorus, trichalcogenides ( TiS 3 ), which are summarized in Table 2. The calculated χ coefficient was listed in Table 2 and the χ of other materials were summarized for comparison, indicating the comparable χ coefficient and application of Bi 2 Se 3 nanoplates, and thus, our temperature-dependent Raman study can be exploited as large nonlocal signals to measure the temperature in graphene—Bi 2 Se 3 heterostructures device [53].

4. Conclusions

In summary, Bi 2 Se 3 single-crystal hexagonal nanoplates with size of 7.50–10.0 μ m were synthesized successfully at large scale by hydrothermal method. XRD, SEM and TEM show that the as-prepared products have pure phase structure, uniform size distribution and high-quality crystallinity. Temperature-dependent micro-Raman spectra show evident Raman mode shift and FWHM broaden with the temperature range from 83 K to 603 K. The temperature dependence of the vibrational modes of Bi 2 Se 3 was found to be almost linear. The temperature coefficient of A 1 g 1 , E g 2 , A 1 g 2 modes were calculated to be −1.258 × 10 − 2 cm − 1 /K, −1.385 × 10 − 2 cm − 1 /K, and −2.363 × 10 − 2 cm − 1 /K, respectively. This low-temperature coefficient is important for obtaining a high figure of merit (ZT). Temperature-dependent Raman study can be exploited as large nonlocal signals to measure the temperature in graphene—a Bi 2 Se 3 heterostructures device. The hydrothermal synthesis of large-scale Bi 2 Se 3 nanoplates with high performance will push its application in field of thermoelectric materials.

Author Contributions

The manuscript was written through contributions of all authors. All authors have given approval to the final version of the manuscript.

Funding

This work was supported by National Natural Science Foundation of China under Grant (No. 11574081, 11374096 and 11074072).

Acknowledgments

Science Research Foundation of Education Department of Hunan Province (No. 15C1091).

Conflicts of Interest

The authors declare no conflict of interest.

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Figure 1. XRD pattern of as-prepared Bi 2 Se 3 nanostructures.
Figure 1. XRD pattern of as-prepared Bi 2 Se 3 nanostructures.
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Figure 2. (a) SEM image. (b) Low magnification TEM image. (c) SAED pattern. (d) HRTEM image. (e) Raman spectrum at room temperature of single Bi 2 Se 3 nanoplate.
Figure 2. (a) SEM image. (b) Low magnification TEM image. (c) SAED pattern. (d) HRTEM image. (e) Raman spectrum at room temperature of single Bi 2 Se 3 nanoplate.
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Figure 3. (a) Raman spectra of Bi 2 Se 3 single crystal in the temperature range of 83–603 K. (b–d) A 1 g 1 , E g 2 , and A 1 g 2 modes of Raman spectra in the temperature range of 83–603 K.
Figure 3. (a) Raman spectra of Bi 2 Se 3 single crystal in the temperature range of 83–603 K. (b–d) A 1 g 1 , E g 2 , and A 1 g 2 modes of Raman spectra in the temperature range of 83–603 K.
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Figure 4. The peak position and temperature (K), FWHM and temperature (K), the peak position and FWHM of A 1 g 1 (a); E g 2 (b); A 1 g 2 (c) Raman active modes in the temperature range of 83–603 K.
Figure 4. The peak position and temperature (K), FWHM and temperature (K), the peak position and FWHM of A 1 g 1 (a); E g 2 (b); A 1 g 2 (c) Raman active modes in the temperature range of 83–603 K.
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Table
Table 1. Comparison of the Raman peak position, FWHM, and temperature coefficient for different Raman modes in the large Bi 2 Se 3 hexagonal single-crystal nanoplates.
Table 1. Comparison of the Raman peak position, FWHM, and temperature coefficient for different Raman modes in the large Bi 2 Se 3 hexagonal single-crystal nanoplates.
Raman ModePeak Position (cm − 1 )FWHM (cm − 1 ) χ (cm − 1 /K)
A 1 g 1 724.83−1.258 × 10 − 2
E g 2 1307.06−1.385 × 10 − 2
A 1 g 2 1747.30−2.363 × 10 − 2
Table
Table 2. The first-order temperature coefficient for the different Raman modes of other two-dimensional materials.
Table 2. The first-order temperature coefficient for the different Raman modes of other two-dimensional materials.
Material Temperature Coefficient ( cm − 1 /K ) Ref
TMDCs χ E 2 g 1 χ A 1 g 2LA(M)A 1 g (M) + LA(M)
MoS 2 (single layer)−0.013−0.016 [54]
MoS 2 (few-layer)−0.016−0.011 [55]
WS 2 (single layer)−0.006−0.006−0.008−0.001[56]
WS 2 (few-layer)−0.008−0.004 [56]
χ A 1 g χ A 2 U 2
MoSe 2 (single layer)−0.0054−0.0086 [57]
MoSe 2 (few-layer)−0.0045−0.0085 [57]
χ E 2 g 1 χ A 1 g A 1 g + LA2A 1 g (M) − LA
WSe 2 (single layer)−0.0048−0.0032−0.0067−0.0067[57]
black phosphorus χ A 1 g χ B 2 g χ A 2 g
black phosphorus−0.008−0.013−0.014 [58]
trichalcogenides χ A 1 g
TiS 3 nanoribbons−0.008−0.018−0.021−0.016[27]
TiS 3 nanosheets−0.022−0.02−0.024−0.017[27]
dichalcogenides χ A 1 g 1 χ E 1 g 1 χ A 1 g 2
Bi 2 Se 3 nanoplates−0.013−0.014−0.024 this work

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Zhou, F.; Zhao, Y.; Zhou, W.; Tang, D. Temperature-Dependent Raman Scattering of Large Size Hexagonal Bi2Se3 Single-Crystal Nanoplates. Appl. Sci. 2018, 8, 1794. https://doi.org/10.3390/app8101794

AMA Style

Zhou F, Zhao Y, Zhou W, Tang D. Temperature-Dependent Raman Scattering of Large Size Hexagonal Bi2Se3 Single-Crystal Nanoplates. Applied Sciences. 2018; 8(10):1794. https://doi.org/10.3390/app8101794

Chicago/Turabian Style

Zhou, Fang, Yujing Zhao, Weichang Zhou, and Dongsheng Tang. 2018. "Temperature-Dependent Raman Scattering of Large Size Hexagonal Bi2Se3 Single-Crystal Nanoplates" Applied Sciences 8, no. 10: 1794. https://doi.org/10.3390/app8101794

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