Size Controlled Synthesis of Germanium Nanocrystals: Effect of Ge Precursor and Hydride Reducing Agent

Carolan, Darragh; Doyle, Hugh

doi:https://doi.org/10.1155/2015/506056

Journal of Nanomaterials

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Abstract Introduction Experimental Results and Discussion Conclusions Acknowledgments References Copyright Related Articles

Research Article | Open Access

Volume 2015 | Article ID 506056 | https://doi.org/10.1155/2015/506056

Size Controlled Synthesis of Germanium Nanocrystals: Effect of Ge Precursor and Hydride Reducing Agent

Darragh Carolan¹and Hugh Doyle¹

Academic Editor: Christian Brosseau

Received17 Mar 2015

Revised02 May 2015

Accepted02 May 2015

Published19 May 2015

Abstract

Germanium nanocrystals (Ge NCs) have attracted increasing attention as a promising alternative to II–VI and IV–VI semiconductor materials as they are cheap, “green,” electrochemically stable, and compatible with existing CMOS processing methods. Germanium is a particularly attractive material for optoelectronic applications as it combines a narrow band gap with high carrier mobilities and a large exciton Bohr radius. Solution-phase synthesis and characterisation of size monodisperse alkyl-terminated Ge NCs are demonstrated. Ge NCs were synthesised under inert atmospheric conditions via the reduction of Ge halide salts (GeX₄) by hydride reducing agents within inverse micelles. Regulation of NC size is achieved by variation of germanium precursor and the strength of hydride reducing agents used. UV-Visible absorbance and photoluminescence spectroscopy showed strong significant quantum confinement effects, with moderate absorption in the UV spectral range, and strong emission in the violet with a marked dependence on excitation wavelength.

1. Introduction

Over the last 25 years, the size dependant optical and electrical properties of semiconductor nanocrystals (NCs) have attracted extensive research into methods to control their size, shape, composition, and surface chemistry [1, 2]. While II–VI and III–V nanomaterials offer facile spectral tuning, high quantum yields, and excellent photostability, concerns about their potential toxicity exist due to their heavy metal content [3, 4]. Germanium is an attractive alternative for optoelectronic applications as it combines a narrow band gap (0.67 eV) and high carrier mobilities ( cm² V⁻¹s⁻¹, cm² V⁻¹s⁻¹) with a large absorption coefficient (ca. cm⁻¹) and exciton Bohr radius (24 nm) [5–7]. Besides its compatibility with current microelectronics processing methods, germanium is also nontoxic, electrochemically stable, and relatively inexpensive [8]. However, the majority of the application areas currently being considered, including chemical sensing [9], field effect transistors [10], and photodetectors [11], require the preparation of Ge NCs in good yield with narrow size distributions and well characterized surface chemistry, as these define many of their photophysical properties.

A number of different synthetic approaches have been investigated towards achieving this objective, including the metathesis reaction of GeCl₄ with Zintl salts [12, 13], reduction of NaGe by ammonium bromide [14], and high temperature decomposition of organogermane precursors [15–17]. Other methods include thermal coreduction of Ge(II) and amido based precursors [18, 19], aqueous phase reduction of GeO₂ powders by NaBH₄ [20], and other high temperature chemical reduction methods [21–25]. Disadvantages associated with these methods include lengthy precursor synthesis, long reaction times, high temperatures and pressures, and extensive postsynthetic purification procedures [8, 23].

The use of microemulsion based synthetic methods has been the most promising due to their ability to control the size, shape, and surface chemistry of Ge NCs. Wilcoxon et al. reported room temperature synthesis of 3–11 nm diameter Ge NCs within reverse micelles via reduction of germanium halide precursors GeX₄ (, Br, or I) with LiAlH₄ [26]. Fok et al. later produced hydride-terminated Ge NCs with an average diameter of 5 nm via reduction of GeI₄ with LiAlH₄ using cetyltrimethylammonium bromide (CTAB) as a surfactant [27]. Subsequent modification of the NC surface by thermally initiated hydrogermylation resulted in alkyl-terminated NCs. Warner and Tilley prepared size monodisperse 5 nm Ge NCs by reducing GeCl₄ within tetraoctylammonium bromide (TOAB) micelles, modifying the surface of the as-synthesized Ge NCs using a Pt-catalysed hydrogermylation reaction to form amine-terminated NCs with covalent Ge-C bonds. This surface modification strategy chemically passivates the nanocrystal surface to prevent oxidation [28]. Prabakar and coworkers later examined the formation of Ge NCs using a series of metal hydrides to reduce GeCl₄ within pentaethylene glycol monododecyl ether (C₁₂E₅) micelles at room temperature [29].

Previously, we reported the synthesis of size monodisperse Ge NCs using a room temperature microemulsion strategy [30, 31]. The surfaces are terminated with a covalently attached monolayer, chemically passivating the surface and allowing for the NCs to be dispersed in a variety of polar solvents; see Scheme 1. Here we report a simple room temperature method for the size controlled synthesis of alkyl-terminated Ge NCs, using different germanium precursors and hydride reducing agents of different strengths to control the NC core diameter between 2 and 10 nm.

2. Experimental

2.1. Materials

Sulphuric acid (95–97%), hydrogen peroxide (30% v/v), hexane (CHROMASOLV grade, ≥97.0%), and n-methyl formamide (99%) were purchased from Sigma-Aldrich Ltd. and stored under ambient atmosphere. Germanium tetrachloride (GeCl₄, 99.99%), germanium tetrabromide (GeBr₄), tetraoctylammonium bromide (TOAB, 98%), lithium aluminium hydride (LiAlH₄, 1 M in THF), lithium triethylborohydride (Li(C₂H₅)₃BH, 1 M in THF), lithium borohydride (LiBH₄, 2 M in THF), lithium tri-sec-butylborohydride (Li[CH(CH₃)CH₂CH₃]₃BH, 1 M in THF), chloroplatinic acid hexahydrate (H₂PtCl₆, >37.5% Pt basis), allylamine (≥99%), 1-heptene (97%), propan-2-ol (99.5%, anhydrous), toluene (99.8%, anhydrous), and methanol (99.8%, anhydrous) were purchased from Sigma-Aldrich Ltd. and stored under inert atmosphere before use. All materials and solvents were used as received.

2.2. Preparation of Ge Nanocrystals

All synthetic manipulations were carried out in an inert atmosphere glove box, with water and oxygen levels kept below 0.1 ppm in order to prevent simple hydrolysis of the Ge precursor. Glassware was cleaned by soaking in a base bath overnight, followed by immersion in piranha solution (3 : 1 concentrated sulphuric acid : 30% hydrogen peroxide) for 20 minutes. In a typical preparation, 2.74 mmol of the surfactant was dissolved in 60 mL toluene in a 2-neck round bottomed flask with continuous stirring. 0.876 mmol of the germanium precursor (GeCl₄ or GeBr₄) was then added to the solution and left to stir for 30 min. Ge NCs were formed by the dropwise addition of 2 mL of the hydride reducing agent over 2 minutes. The solution was then left to stir for 2.5 h. The excess reducing agent was then quenched with 20 mL methanol. The Ge NC surfaces were modified by addition of 100 μL of chloroplatinic acid hexahydrate (0.1 M in propan-2-ol), followed by 2 mL 1-heptene. The Ge NCs were removed from the glove box and the organic solvent was removed by rotary evaporation, yielding a pale yellow powder or oil consisting of TOAB and Ge NCs. The alkyl-terminated NCs were extracted with hexane and filtered first with filter paper and then with PTFE syringe filters (0.45 μm, Acrodisc) to remove all large aggregates. The NCs were washed three times with 100 mL of n-methyl formamide and then with 100 mL deionised water (18.2 MΩcm).

2.3. Characterisation

Transmission electron microscopy (TEM) images and selective area electron diffraction (SAED) patterns were acquired using a high-resolution JEOL 2100 electron microscope, equipped with a LaB₆ thermionic emission filament and Gatan DualVision 600 Charge-Coupled Device (CCD), operating at an accelerating voltage of 200 keV. Data for size distribution histograms was acquired by analysis of TEM images of ca. 300 NCs located at different regions of the grid. NC diameter was determined by manual inspection of the digital images; in the case of anisotropic structures, the diameter was determined using the longest axis. UV-Vis absorbance spectra were acquired using an Agilent 8453 spectrometer or a Shimadzu UV PC-2401 spectrophotometer equipped with a 60 mm integrating sphere (ISR-240A, Shimadzu). Photoluminescence (PL) spectra were recorded on a Perkin Elmer LS 50B luminescence spectrometer. All optical spectra were recorded at room temperature using a quartz cuvette (1 cm) and corrected for the solvent absorption. FTIR measurements were performed on a Bio Rad Excalibur FTS 3000 spectrometer. Samples were drop-cast onto a 32 mm round, 3 mm thick, drilled NaCl plate and left to dry in air.

3. Results and Discussion

Alkyl-terminated Ge NCs were synthesized under inert atmosphere conditions by room temperature reduction of GeCl₄ or GeBr₄ by hydride reducing agents of different reactivities: lithium aluminium hydride (LiAlH₄), lithium triethylborohydride (Superhydride, Li(C₂H₅)₃BH), lithium borohydride (LiBH₄), and lithium tri-sec-butylborohydride (L-Selectride, Li(CH(CH₃)CH₂CH₃)₃BH). Figure 1 shows bright field transmission electron microscope (TEM) images of Ge NCs prepared from GeCl₄ with the different hydride reducing agents. TEM imaging of Ge NCs synthesized in the presence of the strongest reducing agent LiAlH₄ (Figure 1(a)) shows that the Ge NCs are highly size and shape monodisperse, with no evidence of aggregation. Inset in Figure 1(a) is a histogram of Ge NC diameters, determined by analysis of TEM images of 300 Ge NCs located at random locations on the grid. Fitting the histogram to a Gaussian model yielded a mean diameter of 3.0 nm, with a standard deviation of 0.4 nm. Replacing LiAlH₄ with Superhydride or LiBH₄ resulted in an increase in the mean diameter to nm and nm, respectively; see Figures 1(b) and 1(c). These findings are in good agreement with the results reported by Prabakar et al. [29], who reported a similar relationship between Ge NC size and the hydride reducing agent used. L-Selectride produced a bimodal size distribution, with nm and nm Ge NCs formed; see Figure 1(d). These results may be interpreted in terms of the relative strength of the hydride reducing agents used. As the most powerful reducing agent, LiAlH₄ causes rapid consumption of GeCl₄ during the initial burst nucleation phase, resulting in small, size monodisperse Ge NCs. Superhydride and LiBH₄ also yield size monodisperse NCs, but their lower reactivity leads to slightly larger nanocrystals. The sterically hindered L-Selectride consumes the least amount of precursor during the nucleation phase, leaving more precursor material remaining for subsequent diffusional growth in solution, resulting in larger and more polydisperse nanocrystals.

(a)

(b)

(c)

(d)

A similar relationship between size and reducing agent was observed for Ge NCs synthesised with GeBr₄; see Figure 2. LiAlH₄ produced the smallest and most monodisperse NCs, with a mean diameter of 4.0 nm and a standard deviation of 0.4 nm. Superhydride ( nm) and LiBH₄ ( nm) produced larger NCs, while the most polydisperse samples ( nm) were formed with L-Selectride. Comparison of NCs synthesised with different precursor under otherwise identical reaction conditions showed that nanocrystals prepared with GeBr₄ were up to 30% larger than those prepared with GeCl₄. It is known that, in microemulsion based syntheses of metal and semiconductor nanocrystals, the size and shape of the micellar template and thus the resultant crystallite are significantly influenced by precursor anions in accordance with the Hofmeister series [32–34]. These anion effects, allied to the lower Ge-Br bond strength and the greater leaving group ability of the bromide ion, would account for the differences observed.

(a)

(b)

(c)

(d)

High-resolution TEM (HR-TEM) imaging was used along with selective area electron diffraction (SAED) to confirm the crystallinity and establish the crystal phase of the NCs; see Figures 3(a) and 3(b). HR-TEM imaging (Figure 3(a)) showed that the Ge NCs form a continuous crystalline phase, without the presence of packing defects. The lattice fringes shown in Figure 3(a) correspond to a d spacing of 2.0 Å, matching the (220) spacing reported for the germanium unit cell. SAED patterns of the Ge NCs (Figure 3(b)) showed reflections that could be indexed to Ge diamond cubic (Fd3m) lattice at 3.3 Å (111), 2.0 Å (220), 1.7 Å (311), 1.3 Å (331), and 1.2 Å (422), respectively. EDX spectroscopy was employed to determine the elemental composition of the samples. Figure 3(c) shows the energy dispersive X-ray (EDX), where the Ge peaks due to the nanocrystals are clearly seen. Cl and Cu peaks are due to synthetic byproducts and the copper grid support, respectively.

(a)

(b)

(c)

The Ge NC surface chemistry was characterised by FTIR spectroscopy; see Figure 4. The peaks from 3000–2850 cm⁻¹ are attributed to the CH₃ and CH₂ stretching modes of the alkyl chain [31]. The peaks at 1458 and 1260 cm⁻¹ are ascribed to the scissoring and bending of the Ge-C and Ge-CH₂ bonds, respectively, while the strong peak at 1375 cm⁻¹ is assigned to the C-CH₃ symmetric stretching mode [31]. The absence of the characteristic alkene peaks at 3080 and 1640 cm⁻¹, combined with the Ge-C and Ge-CH₂ peaks, confirms the presence of surface-bound heptyl groups. The Ge-OR and the Ge-C stretching modes below 1100 cm⁻¹ are consistent with a covalently attached alkyl layer with some surface oxidation [12, 30, 31]. No significant increase in the intensity of these peaks is observed after storage under ambient conditions, indicating that the NCs are resistant to further oxidation.

The optical properties of the Ge NCs were investigated using UV-Vis absorbance and photoluminescence (PL) spectroscopy. Figure 5 shows the UV-Vis absorption spectrum of Ge NCs prepared using GeCl₄ and LiAlH₄, although similar spectra were obtained for all the nanocrystals reported here. The spectrum shows evidence of strong quantum confinement effects, with a broad absorbance centred at 270 nm with a shoulder at 278 nm, and the presence of a weaker second peak at ca. 330 nm, close to the onset of absorbance at ca. 350 nm (3.5 eV). Similar spectral features have been previously reported in optical spectra of Ge NCs, which were assigned to direct transitions from Γ₂₅ to split energy levels at Γ₁₅ [26, 35]. The significant blue shift in the onset of absorption compared to the bulk Ge band gap energy (0.6 eV) suggests the presence of quantum confined carriers in the nanocrystals. The UV-Vis spectrum recorded 2 months later showed only a small drop in absorbance (see the inset in Figure 4), indicating that the NCs are stable under ambient lighting and atmospheric conditions.

Figures 6(a) and 6(b) show the PL spectra (280 nm excitation) of hexane dispersions of the heptyl-terminated Ge NCs prepared using GeCl₄ and GeBr₄ precursors, respectively. All Ge NCs exhibited a structured luminescence over a narrow spectral range (300–450 nm), with a peak near 330 nm (3.75 eV), similar to previous reports for alkyl-terminated Ge NCs of similar size [31]. While the luminescence intensity decreases with increasing nanocrystal diameter, as would be expected due to the greater contribution of nonradiative exciton recombination pathways, there is no change in the PL spectra, in agreement with our previous results for heptyl-terminated Si NCs prepared using the same synthetic strategy [36]. This size independence implies that exciton recombination is not wholly confined within the nanocrystalline core and that the PL mechanism involves surface states [31, 36], such as the Ge-O_x surface species previously identified (see Figure 4).

(a)

(b)

(c)

(d)

All the NC dispersions show a strong dependence between the wavelength position of the PL maximum and the excitation wavelength; see Figure 6(c). Excitation energies for peak PL intensity (4.4 eV) are considerably higher than the absorption edge (3.5 eV), with a marked dependence between luminescence intensity and excitation wavelength. The wavelength position of the PL maximum red-shifts from 330 nm to 424 nm as the excitation wavelength is increased from 280 nm to 400 nm; see Figures 6(c) and 6(d). This corresponds to an overall red shift in the PL peak position of 94 nm as the excitation wavelength is increased by 120 nm; see Figure 6(d). Increasing the excitation wavelength also results in over a 10-fold decrease in the PL intensity; see also Figure 6(d). These trends are observed in PL spectra for all Ge NCs synthesised.

This excitation wavelength dependence has been observed by a number of groups for alkyl-terminated Ge NCs [8, 12, 14, 15, 18, 31, 36], which has been attributed to the involvement of various surface states in the luminescence process. Dasog et al. unambiguously demonstrated that the blue luminescence in alkyl-terminated Si NCs is due to radiative centres created by nitrogen impurities at the NC surface that provide alternative recombination routes to an indirect bandgap transition [37]. The changes in PL intensity are most likely due to efficient exciton generation at shorter wavelengths, which readily transfer to and recombine at surface states. Excitation at longer wavelengths should result in less efficient exciton generation, which combined with increased transfer to nonradiative trap states, would account for the overall decrease in PL intensity.

4. Conclusions

Solution-phase synthesis and characterisation of size monodisperse heptyl-terminated Ge NCs under inert atmospheric conditions have been demonstrated. Control of Ge NC size was achieved by using germanium precursor with different reactivities and changing the strength of hydride reducing agents used. HR-TEM and SAED confirmed the crystallinity and phase of the NCs while FTIR confirmed that the Ge NCs were well passivated, with some evidence of surface oxidation. UV-Visible absorbance and photoluminescence spectroscopy showed strong significant quantum confinement effects, with moderate absorption in the UV spectral range, and strong emission in the violet, with a marked dependence on excitation wavelength.

Conflict of Interests

The authors declare that there is no conflict of interests regarding the publication of this paper.

Acknowledgments

This work was supported by the European Commission under the FP7 Projects COMMONSENSE (Grant Agreement no. 261809) and SNAPSUN (Grant Agreement no. 246310), as well as the Irish Higher Education Authority under the PRTLI programs Cycle 3 “Nanoscience” and Cycle 4 “INSPIRE.”

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Copyright © 2015 Darragh Carolan and Hugh Doyle. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

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