Open access peer-reviewed chapter

Hydrothermal Synthesis of Zinc Tin Oxide Nanostructures for Photocatalysis, Energy Harvesting and Electronics

Written By

Ana Isabel Bento Rovisco, Rita Branquinho, Joana Vaz Pinto, Rodrigo Martins, Elvira Fortunato and Pedro Barquinha

Submitted: June 9th, 2020 Reviewed: October 1st, 2020 Published: November 19th, 2020

DOI: 10.5772/intechopen.94294

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Abstract

The massification of Internet of Things (IoT) and Smart Surfaces has increased the demand for nanomaterials excelling at specific properties required for their target application, but also offering multifunctionality, conformal integration in multiple surfaces and sustainability, in line with the European Green Deal goals. Metal oxides have been key materials for this end, finding applications from flexible electronics to photocatalysis and energy harvesting, with multicomponent materials as zinc tin oxide (ZTO) emerging as some of the most promising possibilities. This chapter is dedicated to the hydrothermal synthesis of ZTO nanostructures, expanding the already wide potential of ZnO. A literature review on the latest progress on the synthesis of a multitude of ZTO nanostructures is provided (e.g., nanowires, nanoparticles, nanosheets), emphasizing the relevance of advanced nanoscale techniques for proper characterization of such materials. The multifunctionality of ZTO will also be covered, with special attention being given to their potential for photocatalysis, electronic devices and energy harvesters.

Keywords

  • hydrothermal synthesis
  • zinc tin oxide
  • nanostructures
  • nanowires
  • multifunctionality
  • sustainability

1. Introduction

Nanotechnology attracted wide attention over the last decades, leading to a very fast development of materials and processing routes. Different areas such as electronics, cosmetics, medicine/biology, optical systems, energy, and many others, have profited from this rapid growth. Having in mind the environmental issues that we are facing in the modern era, the importance of searching for environmentally friendly, recyclable and low cost nanomaterials and fabrication processes is essential [1].

This has been a concern in strategic areas as large area electronics (LAE), one of the fastest growing technologies in the world, with projected market growth from $31.7 billion in 2018 to $77.3 billion in 2029 [2]. LAE includes many segments (e.g., displays, sensors, logic, memory), which are desired to be seamlessly integrated on virtually any object to create smart surfaces. Due to their good electrical properties, transparency, large area uniformity and good mechanical flexibility, oxide thin films have been crucial materials to advance these concepts [3]. Depending on the metal cations (and on the metal to oxygen ratio), metal oxide thin films can be considered as dielectrics, semiconductors or even conductors [4, 5, 6]. Owing to their remarkable electrical properties, In-based materials, such as ITO (indium tin oxide) and IGZO (indium-gallium-zinc oxide) are currently the multicomponent oxide conductor and semiconductor thin films with larger market relevance in LAE [4, 7]. However, indium is an expensive material, due to its scarcity and high market value, appearing in the current list (2020) of the critical raw materials from the European Commission [8]. The same applies for gallium, another element of IGZO. Therefore, the replacement of these materials is imperative to assure long-term sustainability [1].

This quest for new oxide materials is naturally also transposed for nanostructures, as their fascinating properties will certainly boost even further the demand for oxide (nano)materials in a plethora of industries. Departing from critical cations, ZnO is perhaps the most widely studied oxide nanostructure. Its properties are nowadays well-known and useful for multiple applications, from photocatalysis, to solar cells or biosensors [9]. It can also be prepared by a multiplicity of methodologies, from vapor- to solution-based processes [10]. Multicomponent oxide nanostructures, particularly those based on sustainable materials, have been significantly less studied, but already show great potential to enhance properties and enlarge the range of applications of oxides. As in thin films, a great advantage of these multicomponent materials is the possibility of tuning their properties by adjusting the cationic ratio [11, 12]. Zinc tin oxide (ZTO) is one of the multicomponent oxides that has been explored and has shown very interesting properties when compared with its binary counterparts (ZnO and SnO2). In fact, ZTO was already demonstrated to exhibit similar properties to IGZO in low-temperature thin film transistors (TFTs), while avoiding the use of critical raw materials [13].

This chapter provides a literature review on the hydrothermal synthesis of ZTO nanostructures, the main properties of this material, and its applications, highlighting its multifuncionality.

1.1 Hydrothermal synthesis of ZTO nanostructures

Hydrothermal methods have been widely explored and developed in the last years [14]. This method consists in a chemical reaction in an aqueous solution, under high pressure (> 1 atm) and at temperatures usually ranging between 100°C and 300°C. In case of using non-aqueous solvents, the method is called solvothermal. Typically, the solution is kept inside an autoclave and a conventional oven is used as heat source. The pressure inside the autoclave is dependent both on the temperature and the volume used. This allows for a high energy supply for the reactions even at relatively low temperatures. While the typical nucleation and growth mechanism of the oxide nanostructures in these reactions is thought to consist mainly in dissolution–reprecipitation, these mechanisms are often not well understood.

The synthesis of multicomponent oxide materials such as ZTO is usually easier and more efficient by vapor phase methods, such as chemical vapor deposition and thermal evaporation, than by solution processes, due to the higher temperatures of the former. However, vapor phase methods present drawbacks that are important to consider, such as high temperatures (>700°C) and high costs. On the other hand, while inexpensive and simple, the hydrothermal technique still allows for a well-controlled synthesis of the desired nanostructures’ shape and structure with high reproducibility, thus presenting as an excellent alternative to the conventional physical methods [15, 16]. Additionally, while conventional ovens are typically used as the heat source, microwave-assisted synthesis started recently to be widely explored, enabling reduced synthesis duration due to its more efficient and more homogeneous heat transfer process [17].

1.2 Overview on ZTO nanostructures produced by hydrothermal synthesis

ZTO appears commonly in two main forms, a stable one, Zn2SnO4, and ZnSnO3, a metastable phase. The stable Zn2SnO4 phase is an orthostannate with and inverse spinel structure and is a n-type semiconductor with a band gap of 3.6 eV [18]. ZnSnO3, the metastable phase, can have a rhombohedral structure or a perovskite structure either orthorhombic (−orth) or ordered face centered structure (−fcc) [14, 19]. This phase is a well-known piezo/ferroelectric material and presents a band gap of 3.9 eV [18]. Several ZTO nanostructures such as nanoparticles, octahedrons, nanocubes, nanowires, and nanoflowers, have been produced by hydrothermal synthesis, appearing in both ZnSnO3 and Zn2SnO4 phases. Figure 1 shows examples of Zn2SnO4 and ZnSnO3 nanostructures with different morphologies and dimensions (0D, 1D, 2D and 3D) produced by hydrothermal synthesis.

Figure 1.

Multiple ZTO nanostructures obtained by hydrothermal synthesis, analyzed by scanning electron microscopy (SEM): (a) Zn2SnO4 nanoparticles, from reference [28]; (b) fcc-ZnSnO3 nanoparticles produced by our group; (d) rhombohedral-ZnSnO3 nanowires growth on FTO seed-layer, reprinted with permission from [42], copyright (2020) American Chemical Society; (e) orth-ZnSnO3 nanowires synthesized without employing seed-layers (in form of powder), from reference [43]; (f) orth-ZnSnO3 nanoplates, reprinted with permission from [45], copyright (2020) American Chemical Society; (h) orth-ZnSnO3 hollow spheres, reprinted with permission from [47], copyright (2020) American Chemical Society; (i) orth-ZnSnO3 nanocubes produced by our group; and by transmission electron microscopy (TEM): (c) Zn2SnO4 nanorods, reprinted with permission from [37], copyright (2020) American Chemical Society; and (g) Zn2SnO4 nanoplates, reprinted with permission from [34], copyright (2020) American Chemical Society.

Lehnen et al., for example, reported very small Zn2SnO4 quantum dots (with diameters below 30 nm), produced with a microwave-assisted hydrothermal synthesis, followed by high-temperature annealing [20]. Numerous other reports on Zn2SnO4 nanoparticles have been shown (Figure 1a), either using standard hydrothermal synthesis or solvothermal synthesis [16, 21, 22, 23, 24, 25, 26, 27, 28]. Regarding ZnSnO3 nanoparticles (Figure 1b), several hydro and solvothermal routes have been reported for its synthesis [29, 30, 31, 32]. For instance, Beshkar et al.reported the use of the Pechini method at 80°C to synthesize fcc-ZnSnO3 nanoparticles, followed by a calcination at 700°C for 2 h [33].

Concerning 1D structures, while several reports on Zn2SnO4 nanowires exist, these consist essentially in vapor phase methods, more specifically in thermal evaporation at high temperature (>750°C) [19], showing the difficulty in obtaining the stable phase of ZTO in the nanowire form [34]. This is emphasized by the fact that there are only a few reports for Zn2SnO4 nanowires from hydrothermal synthesis, mostly assisted by seed-layers. For example, Zn2SnO4 nanowires were grown on a stainless steel seed-layer and from Mn3O4 nanowires [35, 36]. Zn2SnO4 nanorods by hydrothermal synthesis were also reported by Chen et al.(Figure 1c), but only organized in 3D flowerlike superstructures [37]. Regarding ZnSnO3, only a few reports for nanowires exist, also consisting typically in physical processes (carbon-thermal reaction, thermal evaporation or CVD processes) [38, 39]. For hydrothermal processing of ZnSnO3 nanowires seed-layers are typically used. Lo et al.employed an FTO thin film as seed-layer for this end (Figure 1d) [40, 41, 42]. A different approach was reported by Men et al.who transformed ZnO nanowires into ZnSnO3 nanowires by a hydrothermal synthesis [41]. Recently, our group demonstrated for the first time ZnSnO3 nanowires obtained by an one-step hydrothermal synthesis without employing any seed-layer (Figure 1e) [32, 43].

2D structures of ZTO have also been reported. Joseph et al.synthesized fcc-ZnSnO3 flakes by a hydrothermal method at only 100°C [44]. Guo et al. produced orth-ZnSnO3 nanoplates (Figure 1f) by a hydrothermal process at 260°C for 24 h [45]. Chen et al.obtained orth-ZnSnO3 nanosheets through a hydrothermal synthesis at 180°C for 12 h, where a precipitate of ZnSn(OH)6 was achieved followed by a calcination at 600°C for 3 h [46]. Zn2SnO4 nanoplates have also been reported, for example, by Cherian et al. (Figure 1g) [34].

There are also several reports regarding 3D ZTO nanostructures. Gao et al.reported the synthesis of ZnSnO3 hollow spheres (Figure 1h) by hydrothermal synthesis at 120°C for 3 h [47]. A commonly reported shape for ZTO nanostructures is the nanocube shape (Figure 1i). For instance, Chen et al.reported a synthesis which could result in ZnSnO3 nanocubes or ZnSnO3 nanosheets, depending on the processing temperature [46]. The octahedron shape is also common, and octahedrons of Zn2SnO4 have been reported by several groups, being these identified as the most stable phase and shape for ZTO nanocrystals. Zn2SnO4 octahedrons constituted by nanoplates can also be formed [48].

While Figure 1 shows the wide range of possibilities offered by hydrothermal synthesis within the ZTO system, it is challenging to obtain structures with a targeted phase (ZnSnO3 or Zn2SnO4 in this case) and shape (e.g. nanosheet or nanowire) [40, 49]. For this end, a comprehensive tailoring of the synthesis parameters is required.

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2. Research methods

Usually the hydrothermal synthesis of ZTO nanostructures is performed inside a teflon-lined stainless-steel autoclave using a conventional oven as heating source. Nevertheless, as previously shown, there are already a few examples of microwave-assisted hydrothermal synthesis of ZTO nanostructures. As an example of a typical method, our synthesis starts with the dissolution of the zinc and tin precursors separately in 7.5 mL of deionized water, followed by their mixture. Then a surfactant (ethylenediamine, EDA) is added, and the solution is magnetically stirred for 30 minutes. The last step is the addition of the mineralizer agent (NaOH). It is observed that milling the precursors before their dissolution in water leads to a more homogeneous result. After the solution preparation, it is transferred into the autoclave and kept in the oven for 24 h at 200°C. After the synthesis, the resultant precipitate (comprising the nanostructures) should be washed several times with deionized water and isopropyl alcohol, alternately, and centrifuged at each time. The nanostructures are usually dried at ≈60°C, in vacuum, for a at least 2 hours [32, 43].

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3. Results and discussion

3.1 Growth mechanism of ZTO nanostructures

3.1.1 Tailoring the chemico-physical parameters of the hydrothermal synthesis

Understanding the influence of each synthesis parameter is a key step in achieving the desired structures. Specifically, considering seed-layer free processes allows evaluation of the intrinsic influence of each synthesis parameter on the nanostructures’ growth. Moreover, the solvent also plays a major role in the process strongly determining the dissolution and diffusion of the species during the synthesis. When the precursors’ solubility is not high enough, precluding an efficient reaction, mineralizer agents can be used (NaOH, KOH, etc.) to increase the solubility of the species [50, 51].

To understand the growth within Zn:Sn:O system it is essential to revise the main equations related with the chemical reactions behind each ZTO phases. The chemical reaction processes for the formation of ZnSnO3 nanostructures have been represented in the literature by the following equations [52]:

Zn2++Sn4++6OHZnSnOH6E1
ZnSnOH6ZnSnO3+3H2OE2

Regarding Zn2SnO4, its formation has been described by different reactions depending on the precursors and solvents involved in the synthesis. For example, Li et al.represented the chemical reaction of Zn2SnO4 nanowires through the equations below, which have been the most common in literature [35].

Zn2++Sn4++6OHZnSnOH6E3
Zn2++4OHZnOH42E4
ZnSnOH6+ZnOH42Zn2SnO4+4H2O+2OHE5

On the other hand, Fu et al. employed a different synthesis method to avoid the use of NaOH, using four different amines (surfactants) instead [53], represented as:

Sn4++3H2OH2SnO3+4H+E6
H2SnO3SnO2+H2OE7
Sn4++6OHSnOH62E8
Zn2++4OHZnOH42E9
SnOH62+ZnOH42Zn2SnO4+4H2O+6OHE10

Several reports show that ZnO and SnO2 crystals can co-exist with ZTO nanostructures when the synthesis parameters differ, even if slightly, from the ideal conditions for ZTO formation. Usually the formation of ZnO (Eq. 11) and SnO2 (Eqs. 1214) is associated with the two alkaline concentration extremes, higher and lower, respectively [54].

ZnOH42ZnO+H2O+2OHE11
Sn4++3H2OH2SnO3+4H+E12
H2SnO3SnO2+H2OE13
H++OHH2OE14

In fact, in our previous work on seed-layer free synthesis of ZTO nanowires, using zinc and tin chloride precursors at a fixed concentration ratio it was shown that while for lower NaOH concentrations SnO2 nanoparticles were obtained, for higher NaOH concentrations ZnO nanowires (mixed with fcc-ZnSnO3 nanoparticles) were achieved, whereas intermediate NaOH concentrations yielded ZnSnO3 nanowires [32]. As shown in Figure 2, a similar trend is seen even when increasing only the NaOH concentration (keeping the precursors’ concentration fixed). This suggests that there is an optimal concentration of the mineralizer. These results agree with those reported by Zeng et al., [54] however, while the authors suggest specific values of pH for obtaining the different structures (SnO2, Zn2SnO4 and ZnO), in our case the pH is much higher due to the presence of ethylenediamine (EDA) which yields a pH of at least ≈ 12, showcasing the trend specifically with the variation of the NaOH concentration and not necessarily the overall pH [32].

Figure 2.

SEM images of resultant nanostructures from synthesis with different precursors’ molar concentrations, i.e., ZnCl2:SnCl4.5H2O:NaOH of (a) 2:1:12 M, (b) 4:2:24 M (from reference [43]) and (c) 8:4:48 M, respectively, while maintaining the same proportion between them. Increasing the precursors’ molar concentrations the materials obtained follow the common trend when increasing only the NaOH concentration: SnO2 nanoparticles, orth-ZnSnO3 nanowires and ZnO nanowires (mixed with fcc-ZnSnO3 nanoparticles).

As mentioned, the precursors’ solubility is a key factor to achieve a well-controlled synthesis. Our previous work showed that for different zinc precursors (zinc chloride or zinc acetate), maintaining the same tin precursor (tin chloride), the reaction differs, being slower and less homogeneous when using zinc acetate, due its lower solubility in the EDA surfactant. The use of surfactants, such as EDA, cetrimonium bromide (CTAB) and sodium dodecyl sulfate (SDS), is very common specially when aiming to induce the growth of 1D nanostructures. Surfactants act as directing growth agents as their molecules aggregate to the surface of the metallic atoms inducing the growth of specific structures/shapes. The solubility of each precursor in the solvents is a key factor for achieving a better synthesis efficiency and homogeneity. This also influences the Zn to Sn precursor ratio required to optimize the achievement of the desired nanostructures.

The duration and temperature of the synthesis are also crucial to determine the achieved nanomaterials. Several reports showed that below 180°C no ZTO phases are obtained, with the intermediate phase ZnSnOH6being produced instead [43, 45]. Zeng et al.showed that to obtain Zn2SnO4 nanostructures a temperature of at least 200°C and 20 h of synthesis are necessary [54]. Meanwhile, Guo et al.observed that 12 h at 260°C are required to produce orth-ZnSnO3 nanoplates for that specific solution process [45]. In our work on the synthesis of orth-ZnSnO3 nanowires, it was observed that syntheses with 12 h at 200°C were necessary for a predominant growth of nanowires. However, for very long synthesis, or at higher temperatures (220°C), the decomposition of the ZnSnO3 phase into the more stable phases starts to occur. It was also concluded that lower energy levels favor the growth of the more energetically stable phases (Zn2SnO4, ZnO and SnO2), the metastable ZnSnO3 is achievable for intermediate energy levels, and for higher energy levels the decomposition (into Zn2SnO4 and SnO2) of ZnSnO3 starts to occur. Higher solution volumes, corresponding to higher pressure in the synthesis, were found to be necessary for obtaining the ZnSnO3 phase. A general growth mechanism for orth-ZnSnO3 nanowires and Zn2SnO4 nanoparticles was proposed and is shown in Figure 3 [43].

Figure 3.

Schematic of the growth mechanism of ZTO nanostructures (ZnSnO3 nanowires and Zn2SnO4 nanoparticles) on a hydrothermal synthesis as a function of the energy available and the duration of the synthesis. From reference [43].

While tailoring the chemico-physical parameters is always necessary, the use of a seed-layer material, usually a thin film, can be very effective in strongly inducing the growth of a desired structure by means of an epitaxial growth mechanism. This approach is commonly used when 1D structures are aimed, as briefly mentioned in the previous section. The selection of the seed material depends on the desired material and structure (phase and shape) and while several reports for different structures exist, the relation between different seed materials and grown structures was not detailed yet in literature. This depends on a complex interrelation between preferential epitaxial growth and thermodynamical stability of the multiple phases and shapes within the Zn-Sn-O system. While the seed-layer route presents advantages for specific applications such as gate-all-around transistors or photocatalysis [55, 56], its absence also brings numerous benefits. For instance, one of the main issues related with the use of seed-layers is the common residuals incorporated in the nanostructures, which are usually undesired for the applications. Also, without seed-layers the synthesis is less complex and this approach brings higher degree of freedom concerning the integration of nanostructures into devices [14, 32, 54].

3.1.2 ZTO phase transformations

Obtaining a single phase and shape of a multicomponent oxide as ZTO is highly desirable due to the different characteristic properties of each phase and shape, still by a hydrothermal synthesis is a challenging process as shown in the last section. In addition, the proper identification of the different possible phases obtained is a difficult task.

As previously presented, ZTO can grow in two different structural phases: Zn2SnO4 and ZnSnO3 (fcc, orth and rhombohedral). Their identification by XRD analysis is challenging since both phases and intermediary compounds show very similar diffraction patterns. While the fcc-ZnSnO3 (ICDD 00–011-0274) has a similar pattern to that of the intermediate phase ZnSn(OH)6 (ICDD 01–073-2384), the orth-ZnSnO3 (ICDD 00–028-1486) pattern can be confused with that of a mixture of Zn2SnO4 and SnO2. In fact, the 00–028-1486 card was deleted from the ICDD database for this reason. Figure 4 shows the XRD peaks of these phases. For clarification, the orth-ZnSnO3 identification was performed by peak indexation, using both treor and dicvol methods, for which the determined crystalline structure was proven to be orthorhombic [32].

Figure 4.

(a) Representation of XRD peaks of ICDD cards of: ZnSn(OH)6, fcc-ZnSnO3, orth-ZnSnO3, Zn2SnO4 and SnO2. Note that the card 00–028-1486 (orth-ZnSnO3) was deleted from ICDD. (b)In-situXRD patterns of ZnsnO3 nanowires during annealing until 850°C. (c) SEM images of the ZnsnO3 nanowires before and after thein-situannealing experiments in XRD.

As previously stated, temperature conditions can induce different phase transformations. For instance, Bora et al.studied the phase transformation of fcc-ZnSnO3 nanocubes into the inverse spinel Zn2SnO4 through Raman analysis during in-situannealing treatment [57]. In this study the phase transformation occurred at 500°C.

Phase transformation in the ZnSnO3 nanowires, synthesized by our group, was investigated by recording XRD patterns in the course of in-situannealing treatment up to 850°C. Figure 4b shows the XRD patterns at different temperatures, where no phase transformation is observable bellow 750°C. At 850°C the characteristic peaks of Zn2SnO4 and SnO2 start to be more pronounced, suggesting the phase transformation described in Figure 3. Nevertheless, a nanowire-like morphology is still obtained after this in-situ annealing experiment (Figure 4c), which was somehow unexpected from the experimental results used to propose the growth mechanism shown in Figure 3.

Thermogravimetry (TG) and differential scanning calorimetric (DSC) measurements up to 1350°C were also performed on ZnSnO3 nanowires to shed light into this. A clear transformation occurred at ≈ 570°C with a mass loss of ≈ 4% (Figure 5), which can be attributed to the expected decomposition of ZnSnO3 into Zn2SnO4 and SnO2. Through XRD patterns (Figure 5b) the orth-ZnSnO3 phase is identified before the annealing, while after the annealing a predominance of SnO2 is noticeable (mixed with Zn2SnO4). SEM images presented in Figure 5c show the nanowires before and after the annealing. After annealing, larger and rounder structures are observed for which energy dispersive X-ray spectroscopy (EDS) analysis showed a predominance of Sn (Sn/Zn ratio of 14.5), in agreement with the XRD analysis.

Figure 5.

(a) TG and DSC curves of as-prepared ZnSnO3 nanowires at a heating rate of 10°C/min at N2 atmosphere. (b) XRD patterns and (c) SEM images of ZnSnO3 nanowires before and after annealing (TG-DSC measurements).

The difference of the decomposition temperature observed between the DSC and the XRD annealing treatments can probably be attributed to the annealing process in both techniques. While the XRD annealing is performed through the heating of a platinum foil (where the nanostructures are placed), in DSC the nanostructures are placed in a melting pot, leading to a more efficient heating and faster decomposition of the ZnSnO3 nanowires.

These results show that when annealing processes are demanded to improve the ZnSnO3 crystallinity, it is important to consider phase transformations carefully. Furthermore, it is noticeable that the temperatures to achieve these phase transformations as a post-synthesis treatment are significantly larger than those required during hydrothermal synthesis, owing to the higher energy provided during synthesis due to the combined effect of temperature and pressure.

3.2 Physico-chemical properties of ZTO nanostructures

The wide array of ZTO nanostructures present different physico-chemical properties which are imposed not only by the structures’ shape but also by their phase (Zn2SnO4 or ZnSnO3).

Concerning the optical properties, ZTO is a wide band gap semiconductor, with reported band gap values of 3.46–3.6 eV for Zn2SnO4 and 3.6–3.9 eV for ZnSnO3 [18, 32, 35, 58]. Nevertheless, these values are not only dependent on the phase, but also on the shape and size of the nanostructures, with higher band gaps for smaller particles due to the quantum confinement effect [16].

While optical properties of nanostructures can be determined simply, their electrical properties are much more challenging to access, especially when considering the properties of a single nanostructure. For this reason, there are only a few reports on electrical characterization of single ZTO nanostructures. While most reports are focused on nanowires with lengths >10 μm (mostly produced by physical processes), smaller ZnSnO3 nanowires (lengths <1 μm), produced in our group by hydrothermal synthesis, were probed individually by using nanomanipulators inside SEM, as shown in Figure 6a. For these, an average resistivity (in vacuum) of 7.80 ± 8.63 kΩ·cm was achieved [32, 59]. When compared to the ≈73 Ω·cm reported by Xue et al.for ZnSnO3 nanowires produced by thermal evaporation (990°C), this resistivity is significantly higher [60], which can be attributed to the higher defect density expected for lower temperature (200°C) and solution-based processes. Concerning Zn2SnO4 nanowires, Karthik et al.reported a resistivity of 6 Ω·cm in vacuum for nanowires synthesized by vapor phase methods at 900°C [61]. Moreover, for Zn2SnO4 nanostructures, which are an n-type semiconductor, mobilities higher than 112 cm2V−1 s−1 have already been reported, highlighting the relevance of using this material for electronic applications [62].

Figure 6.

(a) SEM image showing the tungsten tips of the nanomanipulators, which are contactingin-situdeposited Pt electrodes for the electrical characterization of a single ZnSnO3 nanowire. Atomic force microscopy characterization of individual ZnO and ZnSnO3 nanowires: (b) topographies in noncontact mode, and (c) contact mode tip oscillation as a function of tip-bias ac-voltage. Reprinted with permission from [63]. Copyright 2020 American Chemical Society.

The ZnSnO3 phase is well-known for its piezoelectric properties. A piezoelectric polarization along the c-axis of ≈59 μC/cm2 was reported by Inaguma et al.for ZnSnO3, being much higher than the ≈5 μC/cm2 reported for ZnO [64, 65]. Moreover, the piezoelectric constants of individual ZnSnO3 and ZnO nanowires produced by hydrothermal synthesis were recently determined by piezoresponse force microscopy (PFM) measurements as 23 pm/V and 9 pm/V, respectively (Figure 6b and c) [63]. The enhanced piezoelectric properties reported for ZnSnO3 are related with the higher displacement of the Zn atom in the ZnO6 octahedral cell when compared to the one of the Sn atom in the SnO6 octahedral cell, leading to a higher polarization along the c-axis [66]. Even when compared with other 1D nanostructures produced by hydrothermal synthesis, only the piezoelectric constant of the well-known BaTiO3 (31.1 pm/V) and LiNbO3 (25 pm/V) exceeds the value reported for ZnSnO3. Having sustainability in mind, ZnSnO3 is then a very good alternative to both BaTiO3 and LiNbO3 as these contain critical raw materials [63].

Table 1 summarizes the optical, electrical, and piezoelectric properties of some of the most typical oxide semiconductor nanostructures. These properties show the potential of ZTO compared with other binary and ternary compounds to achieve the desired multifunctionality to meet the concepts of IoT and smart surfaces while avoiding the use of critical raw materials.

PropertiesBand gap (eV)Resistivity (Ω·cm)Piezoelectric constant or polarizationReferences
Material
SnO23.602.17n/a[67]
TiO23.00–3.401.09n/a[68, 69]
ZnO3.371.4–2 × 10−4 *5 nC/cm2, 9–26.7 pm/V[63, 70, 71, 72]
IGZO3.67>106–10−3 *n/a[73, 74, 75]
BaTiO33.476.25 × 109–2.33 × 10831.1 pm/V[76, 77, 78, 79]
ZnSnO33.9073–1.4 × 10359 nC/cm2, 23 ± 4 pm/V[18, 32, 60, 63]
Zn2SnO43.30–3.701.6n/a[18, 58]

Table 1.

Optical, electrical and piezoelectric properties of some of the most typical oxide semiconductor nanostructures.

The properties marked with * are referent to the bulk materials. Abbreviations: n/a – not applicable.

3.3 Application of ZTO nanostructures

The multicomponent nature, together with the wide range of different ZTO nanostructures provide this material system with truly impressive multifunctionality, which will be briefly covered next, mostly focusing on photocatalysis, energy harvesting and electronic applications.

3.3.1 Photocatalysis and piezo(photo)catalysis

Industrial actions and human activities play a negative environmental impact, raising water pollution [80]. Oxide nanostructured materials present great advantages for breakdown of water pollutants, as their band gaps are close to the visible light range and they have high surface-to-volume ratios [81]. Moreover, multicomponent oxides such as ZTO have a higher stability in aqueous environments when compared with binary compounds, which is significantly advantageous for photocatalytic applications [82].

The mechanism of photocatalytic activity of ZTO under UV light can be represented by the equations below [14, 54, 83]:

ZTOe+h+E15
e+h+energyE16
h++H2OH++OH˙E17
h++OHOH˙E18
e+O2O˙2E19
O°2+H+HO˙2E20
OH°O°2HO°2+dyedegradation productsE21

Considering photocatalytic activity under visible light, Jain et al.[84] proposes the following equations:

Zn2SnO4+hvZn2SnO4ecb+Zn2SnO4h+E22
Zn2SnO4ecb+O2Zn2SnO4+O2.E23
Zn2SnO4h++OHOH.E24
O2.+H2OOH+HO2.E25
HO2.+H2OOH.H2O2E26
H2O22OH˙E27
Dye+OH.CO2+H2O+degradation productsE28

Zn2SnO4 nanocrystals were used for the degradation of 50% of reactive red 141 dye in 270 min under sunlight [85]. Different ZnSnO3 structures such as nanowires and nanoplates were already used as photocatalysts for organic pollutants (for example, methylene blue and rhodamine B) [33, 40, 86]. Due to its high optical band gap (3.3–3.9 eV) UV light is usually required to photoactivate this material. Nevertheless, fcc-ZnSnO3 nanoparticles were already reported with a very satisfactory photocatalytic behavior on methylene blue degradation under visible light (0.0156 min−1) [81].

Alternatives to the conventional photocatalytic approach have also been explored, making use of the piezoelectric properties of materials such as ZnSnO3 (nanowires and nanoplates) for piezocatalysis (in the dark) [87] or for piezophotocatalysis (under illumination) [42, 87, 88]. Indeed, piezoelectricity and ferroelectricity (associated with perovskite structures) have shown to play an important role in photocatalysis, since the photogeneration of electron–hole pairs is enhanced by the dipole moment formed by the polarization electric field across polar materials [89, 90]. A schematic representation of the piezocatalytic mechanism is presented in Figure 7b and shows the influence of the characteristic polarization of the piezoelectric materials, which contributes to the generation of hydroxyl radicals and consequently degradation of rhodamine B. The dye degradation was achieved in 2.5 h, with a degradation rate of 4.5 × 10−2 min−1 [87].

Figure 7.

(a) Piezocatalysis using ZnSnO3 nanoparticles under ultrasound exposure. (b) Schematic of the piezocatalytic mechanism. Reprinted with permission from [87]. Copyright (2020) American Chemical Society.

Other interesting applications of photocatalytic properties have been reported, such as the photocatalytic inactivation of Escherichia coliusing ZTO nanocubes under visible light. Only a 10% surviving rate was found for the bacteria, whereas the absorption of the visible light was attributed to the inherent surface defects enhancing the absorption edge in the visible region [82]. With this in mind, lower cost methods for nanostructure production (as hydrothermal methods), which typical result in more defective structures, might be advantageous for these applications as defect levels near the band edges may increase the absorption for lower energy levels.

3.3.2 Piezoelectric energy harvesting with ZTO nanostructures

Nanogenerators are devices that can convert external stimulus into electrical energy, being highly interesting for smart and self-sustainable surfaces, as they can be used for sustainable energy sources, biomedical systems and smart sensors [91]. Due to its excellent ferroelectric and piezoelectric properties, different ZnSnO3 nanostructures (i.e., nanowires, nanoplates, nanocubes) have been widely explored for energy harvesting devices and sensitive human motion sensors, through their piezoelectric (induction of electrical charge by the applied mechanical strain) and piezoresistive (electrical resistivity change by the applied mechanical strain) effects, respectively [45, 66, 92, 93, 94]. The fcc-ZnSnO3 nanocubes have been the most popular ZTO structures for these applications. For instance, Wang et al. reported the nanogenerators of fcc-ZnSnO3 nanocubes mixed with polydimethylsiloxane (PDMS), reaching a maximum output of 400 V, 28 μA at a current density of 7 μA·cm−2 [95]. While, Paria et al.mixed fcc-ZnSnO3 nanocubes with polyvinyl chloride (PVC), achieving a maximum output of ≈40 V and ≈1.4 μA, corresponding to a power density of 3.7 μW·cm−3 (Figure 8a) [94].

Figure 8.

Hybrid nanogenerators of: (a) a composite film based on fcc-ZnSnO3 nanocubes and PVC. Reprinted with permission from [94], copyright 2020 American Chemical Society; and (b) a composite film based on orth-ZnSnO3 nanowires and PDMS. (c) Schematic of the charge generation mechanism in the micro-structured devices of (b). Images (b) and (c) were reprinted with permission from [63], copyright 2020 American Chemical Society.

ZnSnO3 nanoplates were also applied for nanogenerators. Guo et al.reported produced nanogenerators fabricated with orth-ZnSnO3 nanoplates embedded in flat films of PDMS, reaching voltage and current outputs of 20 V and 0.6 μA, respectively, under bending stress [45]. More recently in our group, orth-ZnSnO3 nanowires were mixed with PDMS to fabricate nanogenerators of micro-structured composites (Figure 8b) [63]. In the same work, a charge generation and displacement mechanism was proposed, as depicted in Figure 8c. Briefly, the micro-structures induced in PDMS are suggested to improve the force delivery to the nanowires, enhancing its piezoelectric signal, while bringing also a triboelectric contribution to the nanogenerator output. This results in an output voltage, current and instantaneous power of approximately 9 V, 1 μA and 3 μW·cm−2, respectively, when applying a force of only 10 N. For higher forces the devices were capable to reach outputs around 120 V and 13 μA, which was shown to be enough energy to light up LEDs and several small electronic devices [63].

3.3.3 Electronic applications

Electronic applications are always a relevant drive for materials. Multicomponent semiconductor nanostructures as ZTO are particularly interesting for these applications, with wide band gap semiconductors allowing for high-power and high-frequency operations [50]. Field-effect transistors (FETs) are the key elements enabling today’s electronics, being 1D nanostructures particularly interesting in this regard, given the easiness of confining migratory direction of charge carriers through its length, i.e., between source and drain electrodes. Indeed, 1D nanostructures have already proven great usefulness for the upcoming generations of semiconductors in FETs [96]. While several reports already demonstrated ZTO as a candidate for replacement of IGZO in thin film technologies [13], similarly, ZTO is also one of the most promising multicomponent metal oxides for transistors with nanostructures [62]. Demonstrations of discrete Zn2SnO4 nanotransistors have already been made using nanotransfer molding of ZTO inks followed by annealing at 500°C, or by simple pick-and-place approach of drop-casted ZTO nanowires prepared by CVD above 700°C and by thermal evaporation at 1000°C [39, 97, 98]. While the achievement of on/off ratio ≈106 and field-effect mobility ≈20 cm2/Vs is a good demonstration of the ZTO’s potential, transistors using ZTO nanostructures synthesized by solution processes have not been reported yet. Furthermore, these nanostructures have also been used for the resistive switch layer in the emerging type of memory devices known as memristors. Reports show ZTO as the active material in memristors in the form of both Zn2SnO4 nanowires and ZnSnO3 nanocubes, being the latter especially relevant for this application due to its ferroelectric properties. Properties such as high off/on ratios (>105), long retention times (>5 months) and fast response speeds (<20 ns) are obtained for these devices [99, 100].

Transforming ZTO or other nanostructures into well-established LAE semiconductor materials, while highly desirable from the performance and functionality point of view, will still require significant advances in reliable techniques for alignment and density control in transparent (and flexible) substrates [101].

3.3.4 Other applications

Besides the applications briefly presented above, ZTO nanostructures have also been widely used in sensing applications, with gas sensors being the most popular [102]. Their small crystallite size, high surface-to-volume ratios and surface reactivity result in enhanced sensitivities/selectivity, with multicomponent materials typically presenting smaller response times and superior stabilities compared to binary compounds [103]. Moreover, the implementation of these nanostructures in sensors allows miniaturization of the devices, as well as cost reduction. ZnSnO3 has been reported as an excellent humidity sensor, in different nanostructure forms such as nanoparticles or even in composites of ZnSnO3 nanocubes and Ag nanowires [29, 104]. Additionally, ZnSnO3 nanoparticles were used as electrochemical biosensors for label free sub-femtomolar detection of cardiac biomarker troponin T and a composite of Zn2SnO4 nanoparticles and graphene was used for morphine and codeine detection [105, 106]. Recently, Durai et al.. reported ultra-selective sensors, based on ZnSnO3 nanocubes modified glassy carbon electrode (GCE), for simultaneous detection of uric acid and dopamine through differential pulse voltammetry technique [107]. Zn2SnO4 and ZnSnO3 nanostructures of different shapes such as nanoparticles, nanowires and nanocubes, have also been widely explored as photoconductors [23, 108, 109, 110, 111]. While the optical band gap of these materials is typically in the UV energy levels (hence their transparency in visible range), quantum confinement effects or even defect levels near the band edges can be explored to increase the absorption for lower energy levels. Other applications that have been explored using ZTO nanostructures are related with energy storage and conversion. Zn2SnO4 has been widely used as photoanode for dye solar cells in different nanostructure morphologies such as nanoparticles and nanowires [21, 35]. Cherian et al.reported the performance of nanowires and compared with nanoplates of Zn2SnO4 for Li-batteries [34]. Supercapacitors (SC) have also started to be explored using ZTO nanostructures, with Bao et al.having reported the use of Zn2SnO4/MnO2 core shell in carbon fibers showing a capacitance of 621.6 F·g −1 [112].

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4. Conclusions

Expanding LAE to IoT and smart surface concepts requires an increasing number of objects to have embedded electronics, sensors and connectivity, driving a demand for compact, smart, multifunctional and self-sustainable technology with low associated costs. While nanomaterials are thought to be able to meet these requirements, playing an important role in the future technological world, low cost and sustainable technologies are demanded. For this, both low cost fabrication methods and sustainable materials must be considered. This chapter shows the versatility of the hydrothermal method to control the growth and morphology of zinc tin oxide (ZTO) nanostructures, and the variety of shapes that can be produced for each of the different ZTO phases. Compared to other preparation methods, especially vapor phase methods, hydrothermal synthesis reveals a large set of advantages from both research and industrial viewpoints. First, while the multitude of parameters to control requires an in-depth understanding of their role in the final products, it also brings enormous flexibility to tune the synthesis process for the desired results. Also, it can be performed at low temperature (< 200°C), which is compatible with a wide range of substrates for direct growth, while assuring lower costs. This links perfectly with the demonstrated upscaling capability of hydrothermal synthesis which is a crucial aspect for industrial implementation.

Furthermore, a summary of exciting results that have been reported regarding application in devices of these ZTO nanostructures over the past few years is presented. The multifunctionality of this material system is highlighted by its successful implementation in energy harvesters, photocatalysis, electronic devices, sensors, and others.

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Acknowledgments

The authors would like to thank Ana Pimentel for the TG-DSC measurement.

This work is funded by FEDER funds through the COMPETE 2020 Programme and National Funds through the FCT – Fundação para a Ciência e a Tecnologia, I.P., under the scope of the project UIDB/50025/2020, and the doctoral grant research number SFRH/BD/131836/2017. This work also received funding from the European Community’s H2020 program under grant agreement No. 716510 (ERC-2016-StG TREND), No. 787410 (ERC-2018-AdG DIGISMART) and No. 685758 (1D-Neon). This work is part of the PhD Thesis in Nanotechnologies and Nanosciences defended by Ana Rovisco at FCT-NOVA entitled “Solution-based Zinc Tin oxide nanostructures: from synthesis to applications” in December 2019.

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Conflict of interest

The authors declare no conflict of interest.

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Written By

Ana Isabel Bento Rovisco, Rita Branquinho, Joana Vaz Pinto, Rodrigo Martins, Elvira Fortunato and Pedro Barquinha

Submitted: June 9th, 2020 Reviewed: October 1st, 2020 Published: November 19th, 2020