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Article

Synthesis of Orthorhombic Tin Dioxide Nanowires in Track Templates

by
Zein Baimukhanov
1,
Alma Dauletbekova
1,*,
Diana Junisbekova
1,
Valeriy Kalytka
2,
Abdirash Akilbekov
1,*,
Aiman Akylbekova
1,
Guldar Baubekova
1,
Gulnara Aralbayeva
1,
Assyl-Dastan Bazarbek
3,
Abay Usseinov
1 and
Anatoli I. Popov
4
1
Department of Technical Physics, L.N. Gumilyov Eurasian National University, Satpayev Str. 2, Astana 010008, Kazakhstan
2
Faculty of Energy, Automation and Telecommunications, Abylkas Saginov Karaganda Technical University, Karaganda 100027, Kazakhstan
3
Department of Space Technique and Technology, L.N. Gumilyov Eurasian National University, Satpayev Str. 2, Astana 010008, Kazakhstan
4
Institute of Solid State Physics, University of Latvia, Kengaraga 8, LV-1063 Riga, Latvia
*
Authors to whom correspondence should be addressed.
Materials 2024, 17(6), 1226; https://doi.org/10.3390/ma17061226
Submission received: 3 February 2024 / Revised: 21 February 2024 / Accepted: 28 February 2024 / Published: 7 March 2024
(This article belongs to the Section Advanced Nanomaterials and Nanotechnology)
Browse Figures
Versions Notes

Abstract

Electrochemical deposition into a prepared SiO2/Si-p ion track template was used to make orthorhombic SnO2 vertical nanowires (NWs) for this study. As a result, a SnO2-NWs/SiO2/Si nanoheterostructure with an orthorhombic crystal structure of SnO2 nanowires was obtained. Photoluminescence excited by light with a wavelength of 240 nm has a low intensity, arising mainly due to defects such as oxygen vacancies and interstitial tin or tin with damaged bonds. The current–voltage characteristic measurement showed that the SnO2-NWs/SiO2/Si nanoheterostructure made this way has many p-n junctions.

1. Introduction

Contemporary materials science is currently focused on developing new materials and methods for oxide photonics, sensors, and optoelectronics [1]. This trend is aimed at creating smaller device sizes, with a particular focus on one-dimensional nanowire-based optoelectronic devices such as emitters [2,3], detectors [4,5], and transistors [6,7]. These devices are currently being actively developed.
SnO2 is an oxide semiconductor that is widely recognized for its unique electrical and optical properties. At 300 K, it has a band gap (Eg) of 3.6 eV and exhibits n-type conductivity. Due to its exceptional characteristics, including high electrical conductivity, low electrical resistance, and excellent optical transparency in the visible spectrum, SnO2 has been extensively studied for various applications. It is commonly used in the manufacturing of transparent conductors [8], transistors [6,7,9], optoelectronic devices [10,11], gas sensors [12], and more.
There are various types of tin oxide in nanoform. By constructing low-dimensional nanostructures on semiconductor oxides, it is possible to create and design new material systems with unique properties. Nanowires (NWs), for example, can support nanoparticles, other nanowires, and nanosheets, providing access to designs that were previously unattainable with conventional thin-film technology. Molecular beam epitaxy (MBE) and chemical vapor deposition (CVD) are regulated processes used to produce high-quality nanomaterials. The interaction between the physical characteristics of oxides and the 1D shape of NWs makes oxide wide-gap semiconductors (WBGs) an excellent technological foundation.
Producing oxide nanomaterials with consistent morphologies and physical properties is a major challenge due to their lack of repeatability. Unlike group III-V semiconductors, manufacturing such structures is often complex and poorly understood. However, self-assembly mechanisms can provide the necessary repeatability and facilitate the “bottom-up” fabrication method [13].
One of the simplest techniques for creating nanowires is using nanoporous templates. The template synthesis method, which utilizes porous materials such as track membranes made of polyethylene terephthalate (PET), is a potential strategy for creating nanostructures. Electrochemical deposition can produce Fe/Co nanotubes on these PET membranes [14]. Other studies have produced Ni/Fe nanotubes and silver/gold nanoparticle-embedded nanotubes [15,16]. In a separate study, a simple process for electrochemical deposition in PET membranes was proposed to create nanotubes made of zinc. That study found that by annealing the resulting nanotubes, it is possible to control the production of an oxide phase in the nanostructure.
Due to their compatibility with existing silicon technology and their potential for application in the creation of track templates, thin nanoporous SiO2 layers incorporated into silicon wafers present intriguing advantages for nanotechnology. These templates, which are made up of nanoporous arrays that have been etched onto the location of latent tracks in SiO2, can be filled with a range of substances and composites.
The resultant structures could be used as low-temperature magnetic field sensors [17], biosensors [18,19], active electrical circuit elements [20], and more. These structures on Si wafers were produced using SHI track technology, which is only one illustration of the potential this novel strategy offers.
Due to the self-organization of WBG inside nanochannels, different structures can be obtained using this method. The template was created from a SiO2/Si structure using track technology, which includes irradiation with swift heavy ions and a chemical etching process [21,22]. Next, filling the nanopores with various materials is carried out. In our case, we are considering the possibility of tin dioxide precipitation.
An attractive aspect of template synthesis [23] is the ability to tailor a nanomaterial’s physical, chemical, and electronic properties through controlled manipulation of morphology, pore density, shape, and size. Our works demonstrate successful template synthesis of ZnO [23], CdTe [24], and ZnSe2O5 [25], resulting in stable phases of these compounds as well as phases that are typically only obtainable under special conditions.
This study aimed to form SnO2-NWs/SiO2/Si nanoheterostructures with arrays of p-n junctions and experimental/theoretical investigations of physical properties of obtained nanostructures. In order to corroborate our experimental results and better understand the electronic structure of the resulting SnO2 nanostructures, we simulated the electronic band structure along with the total density of states using the CRYSTAL-17 program [26]. Calculation details are presented in the Materials and Methods section.

2. Materials and Methods

In the present work, the SiO2/Si (p-type) structure was formed by thermal oxidation of silicon substrate in a wet oxygen atmosphere at T = 900℃. According to ellipsometry, the thickness of the oxide layer was 700 nm. Irradiation of 10 × 10 mm2 SiO2/Si samples to create latent tracks in the SiO2 layer was carried out at a DC-60 cyclotron (Joint Institute for Nuclear Research (JINR) Dubna, Russia). The samples were bombarded at normal incidence with 200 MeV 132Xe ions to a fluence of 108 cm−2.
Etching in 4% aqueous HF solution was carried out to form nanoporous SiO2 layers irradiated with Xe ions. The etchant included m(Pd) = 0.025 g. The process of etching was performed at room temperature for a certain duration. The nanopore sizes were controlled depending on the etching time. After treatment in HF, the samples were washed in deionized water (18.2 MΩ). Electrochemical deposition (ECD) and chemical deposition (CD) were used to fill the nanochannels [27]. The template synthesis was carried out immediately after sensitization of surface and etching. The template synthesis (chemical and electrochemical deposition of materials) was a universal and simple method of receiving arranged arrays of nanostructures in matrix channels.
The electrolyte used to obtain SnO2-NWs/SiO2/Si, contained 6 g/L SnCl2–25 mL H2O–2 mL HCl. The composition solution was stirred using a magnetic stirrer while adding hydrochloric acid dropwise until the pH was between 2 and 4, stirring continuously until a clear solution formed. For the ECD process, a cell that was specifically prepared and a VersaStat 3 potentiostat were utilized. The ECD process was carried out at room temperature. A two-beam scanning microscope controlled the filling of nanopores, the Zeiss Crossbeam 540 (Jena, Germany).
X-ray diffraction analysis (XRD) provided detailed information on the structure and phase composition of the samples. Diffractograms were recorded using a Rigaku SmartLab X-ray diffractometer (Rigaku, Tokyo, Japan) with a high-energy resolution 2D HPAD detector HyPix3000 (Rigaku, Tikyo, Japan) in the 2θ range from 5 to 70° at 40 kV. When analyzing the diffraction patterns, we used TOPAS 4.2 software and the international ICDD database (PDF-2 Release 2020 RDB) to identify the phase composition and unit cell parameters of substances. This method enabled us to determine the structures of over 200,000 different compounds.
Photoluminescence spectra were measured at room temperature using a spectrofluorometer CM2203 (Solar, Minsk, Belarus) in the spectral range from 320 to 600 nm when excited by light with a wavelength of λ = 240 nm. Using two double monochromators ensured a minimum level of interference, guaranteeing high measurement accuracy.
A VersaStat 3 potentiostat/galvanostat (Ametek, Berwyn, PA, USA) was used to study the electrical properties of the resulting nanowire arrays. Current–voltage characteristics were measured from an array of filled nanochannels with an area of 0.7 cm2.
As noted above, we performed hybrid “large scale” DFT calculations of the structural and electronic properties of obtained SnO2 nanostructures in the framework of a periodic linear combination of atomic orbitals (LCAO) approximation. All calculations were made using the primitive crystal cell containing 24 atoms. The all-electron Gaussian-type basis sets (BS) for Sn and O atoms were taken from refs. [28,29], respectively. The total energy convergence threshold for the self-consistent field (SCF) procedure was chosen at 107 Hartree for structure relaxation calculations. The exchange and correlation effects were treated by using a B3LYP functional form (i.e., Becke’s three-parameter hybrid exchange functional [30] and Lee, Yang, Parr correlation functional [31]). It is worth noting that the hybrid B3LYP functional allows us to perform very accurate calculations of the band gap which are in good agreement with the corresponding experimental values. The integration of the reciprocal space was performed with a Pack–Monkhorst 4 × 4 × 4 grid. The effective atomic charges were determined using the Mulliken population analysis [32].

3. Results and Discussion

3.1. SEM and XRD Analysis of Deposited Samples

Figure 1 shows SEM images of the surface after deposition.
Figure 1 shows the SEM images of the surface after electrochemical deposition. SEM image analysis revealed nanopore diameters ranging from 519 nm to 562 nm. The amount of filled nanochannels was 87%.
According to XRD data (Figure 2), electrochemical deposition in a chloride solution into a SiO2/Si track template led to the creation of SnO2 nanowires with an orthorhombic structure and Pbca (61) space group symmetry. The results of the XRD analysis of the sample are summarized in Table 1.
We calculated the band structure along the highly symmetric k-points of the Brillion zone along with the density of states (Figure 3). The lattice parameters of relaxed crystal geometry were also calculated (see Table 1) The maximum of the valence band and the bottom of the conduction band were located at the Г-point with a band gap of 3.76 eV, which had good agreement with the previous studies using GGA-PBE [33] and the augmented plane wave (APW) methods [34]. It is worth noting, however, that various experimental estimates of the band gap vary from 1.7 to 4 eV [35,36,37]. Nagasawa et al. [38] studied the temperature dependence of the absorption edge for two polarizations of light; they showed a strong dependence of the optical adsorption edge on both factors. For both polarizations, the band gap decreases with increasing temperature. Figure 3 shows good agreement between theory and experiment. In particular, we find a valence band width of ~8 eV in good agreement with both experimental data (7.5 eV reported in ref. [39]) and previous first-principles calculations (7.9 eV and 8.8 eV reported in ref. [40] using PSP and USP, respectively). O-2p states mainly form the uppermost valence band, while the bottom of the conduction band is mostly the result of the contribution of Sn-4d orbitals with a hybridization of O-2p orbitals.
It is known that SnO2 crystallizes as a single crystal in the rutile, tetragonal structure (cassiterite) phase SnO2-(T). Rutile was typically used as the crystalline phase when this material was created as a nanostructure. However, as with many other materials, the crystal lattice changes under special conditions, such as high pressure, and the crystallographic phase becomes different. The study of [41] was one of the first to synthesize the orthorhombic phase SnO2-(O) of tin dioxide. The synthesis process was carried out using a split-sphere high-pressure vessel featuring an inner and outer layer. The container holds the sphere with samples, which is immersed in liquid. As the fluid pressure rises, the sphere is uniformly compressed. The samples in the center of the sphere are subjected to controlled pressure. The temperature was maintained by a small furnace tube. In this experiment, the SnO2-(O) polymorph with lattice parameters a = 4.714 Å, b = 5.727 Å, and c = 5.214 Å was synthesized at a pressure of 15.8 GPa and a temperature of 800 °C.
Unique studies of polymorphic transformations in SnO2 (cassiterite) were conducted in [42]. In situ, XRD analysis of the structure at increasing pressure and temperature showed the existence of four phase transitions up to 117 GPa. Cassiterite powder was mixed with 10 wt% Pt and located into a special cell. Platinum was used as a laser absorber and pressure standard. Starting from the rutile structure, the sequence of polymorphic transformations is as follows: rutile-type with space group P42/mnm transforms to CaCl2−type, Pnnm, which then transforms to pyrite-type, Pa3. The pyrite-type, Pa3, then transforms to ZrO2 orthorhombic phase I (O I), Pbca, and the last transformation is to cotunnite-type (Pnam) orthorhombic phase II (O II). The first three polymorph phases were found to be in general agreement with the results of previous studies. The orthorhombic phase O I and orthorhombic phase O II were observed in SnO2 for the first time. So, the (O I) Pbca phase formed at room temperature and 50–74 GPa pressure. The lattice parameters for this structure were determined and are as follows: a = 9.304 Å, b = 4.893 Å, and c = 4.731 Å. These values closely resemble those obtained in track template synthesis by ECD and our theoretical calculations (Table 1). Thus, the template synthesis (ECD) yielded orthorhombic SnO2 with a ZrO2-type crystal structure (orthorhombic phase I). We created a unit cell of SnO2 Pbca using our own data (Figure 4).
As can be seen, orthorhombic SnO2 is more difficult to fabricate as high pressure and temperature are required. But creating orthorhombic SnO2 in nanoforms, in the form of thin films, turns out to be a more affordable option. Several research groups have successfully created orthorhombic SnO2 thin films using different techniques at moderately low pressures and temperature [43,44,45,46,47,48,49].
Only a small fraction of the studies mention the preparation of the orthorhombic phase of tin dioxide nanowires, although many papers are devoted to the preparation of tin dioxide NWs (see [50,51,52,53] and references cited therein). SnO2 nanoribbons/nanowires were synthesized using elevated temperature synthesis techniques in inert Ar gas [54,55]. The authors suggest that orthorhombic SnO2 may be the result of product formation in an oxygen-deficient environment. The description of atypical structures in nanowires created using a template method or by adding catalytic in a vapor–liquid–solid method for different materials is presented in [56,57,58]. The authors of [59] conducted a study on the synthesis of pure single-crystal orthorhombic SnO2 as well as SnO2 nanowires that were decorated with cassiterite nanoclusters.
Based on our literature analysis, we found that using the template synthesis method provides us with the opportunity to successfully obtain tin dioxide with ZrO2 orthorhombic phase I (O I), Pbca nanowires, and nanoheterostructure (SnO2-NWs/SiO2/Si).

3.2. The Photoluminescence (PL) End Electrical Properties of Orthorhombic SnO2-NWs/SiO2/Si

Photoluminescence (PL) techniques are useful in detecting nanocrystal structure, defects, and impurities. Previous studies on the luminescence of SnO2 nanocrystals can be found in the following articles and references therein [60,61,62,63,64,65,66,67,68,69,70,71,72,73,74,75,76].
The PL of SnO2-NWs/SiO2/Si was investigated in the spectral range from 300 to 600 nm under excitation at λ = 240 nm. In Figure 5, the photoluminescence spectrum of SnO2-NWs/SiO2/Si structures is represented through Gaussian decomposition. We also subtracted the luminescence of amorphous silica.
The photoluminescence is caused by crystal defects or electronic transitions related to oxygen vacancies or interstitial tin, etc. They arise in the band gap during growth. Oxygen vacancies are the most common defects and usually act as emitting centers in luminescence processes. Oxygen vacancies are found in semiconductor oxides in three charge states: V O 0 , V O + and V O 2 + [70]. V O 0 is a very shallow donor; it corresponds to a peak of 2.39 eV (518.76 nm) [71], and most oxygen vacancies will be in the paramagnetic state V O + with peak at 2.58 eV (480 nm) [67,72]. The transition from the triplet state to the ground state for V O 0 may be associated with blue emission at a maximum of 2.8 eV (442.8 nm) [73]. Nanostructured SnO2 was found to have a similar observation in its PL spectrum [74]. The luminescence centers responsible for the maximum violet emission at 2.9 eV (427.53 nm) can be attributed to interstitial tin or tin with damaged bonds [65,66,67,68,69]. The peak at 2.15 eV (575 nm) is caused by trap emission from defect levels in the band gap, such as oxygen vacancies, rather than a direct electronic transition. In this SnO2-NWs/SiO2/Si nanoheterostructure, oxygen vacancies act as luminescent centers, forming defect levels that capture electrons from the valence band and contribute to luminescence [75,76]. It is probable that the observed peak of 2.23 eV (554 nm) is a result of oxygen vacancies that occur during deposition, as reported in studies [77,78]. Similar outcomes were discovered in the examination of SnO2 nanobelts [79] and beak-shaped nanorods [80]. It is widely understood that oxygen vacancies are the most frequent type of imperfection and often act as emitting defects in luminescence occurrences. Indeed, from the analysis of the PL spectrum, we can see that the dominant defects are oxygen vacancies, but not defects associated with Sn. This indicates oxygen deficiency. This deficiency can be explained by the electrochemical deposition conditions shown in Figure 6a.
On the inner walls of nanochannels in amorphous silicon dioxide there are silicon and oxygen ions and their vacancies. When an external electric field is applied, the top layer of silicon is charged negatively, and the created field prevents the free movement of oxygen radicals. At the same time, tin ions rush into the channel and interact with oxygen ions on the channel walls (amorphous SiO2) to form tin dioxide under conditions of oxygen deficiency, forming orthorhombic tin dioxide with various oxygen-vacancy defects. This also explains the low number of defects associated with tin.
To confirm the contact between SnO2 nanowires and silicon substrate, which can be clearly seen in Figure 6b, the current–voltage characteristics (CVCs) of the SnO2-NWs/SiO2/Si structure were investigated. To confirm the formation of junctions more clearly, a cross-sectional view is shown in Figure 7. It appears that SnO2 nanowires are tightly packed onto a silicon substrate and form junction structures. The CVCs were measured from an array of filled nanochannels with an area of 0.7 cm2. The CVCs were investigated using a second-order polynomial fitting [25].
Based on Figure 7, it is evident that the CVCs behave like a diode. This means that the current increases exponentially as the voltage increases in the forward direction. The current is attributed to electrons, as the Si substrate is of p-type. By analyzing the CVCs, it can be inferred that the SnO2-NWs/SiO2/Si structure has an electronic type of conductivity. We can determine the conductivity of nanowire arrays using Formula (1):
σ = d I d U   l A ,
where l is the length of the nanowire (approximately corresponds to the thickness of the oxide layer of the substrate, about 700 nm); A —area;   d I / d U —tangent of the angle of inclination I–U. Values for A = 2 π r 2 = 57174   nm 2 , σ = 1.5 × 10 8   Om − 1 · cm − 1 . Therefore, we can discuss the formation of a series of p-n junctions.
The conductivity of polycrystalline samples can be explained using diffusion and thermoemission models. When the barrier width W is much larger than the free path length of carriers L, we can use the diffusion theory. On the other hand, the thermoelectron emission model is applied when L > W. According to this model, only those carriers whose kinetic energy is greater than the barrier height can cross the boundary. If we assume that we have barriers of the same type, and on average a voltage of V/m is applied (where m is the number of barriers between the electrodes, and V is the interelectrode voltage), then we can use the following equation to determine the height of the potential barrier φ and the number of barriers m in series [81]:
I = I 0 exp − e φ − V m / k T ,
This equation is also used to analyze current transfer in polycrystalline gallium phosphite [82,83]. The number of barriers can be estimated using the Formula (3):
m =   H h k ,
where H is the height of the nanopore and hk is the linear size of the nanocrystallite. The average value of the lattice parameters from Table 2 can be used for hk.

4. Conclusions

We successfully obtained vertical nanowires of tin dioxide (SnO2) through electrochemical deposition into a SiO2/Si track template; they had an orthorhombic ZrO2 crystal structure with the lattice parameters a = 9.97195 Å, b = 5.11601 Å, and c = 5.03283 Å.
We calculated the band structure along the highly symmetric k-points of the Brillion zone along with the density of states. The lattice parameters of relaxed crystal geometry were also calculated and matched well with our experimental data. The maximum of the valence band and the bottom of the conduction band were located at the Г-point with a band gap of 3.76 eV, which had good agreement with previous studies.
The study of the PL spectrum showed a broad emission band in the spectral range of 400–600 nm, in which it was found that the dominant defects were oxygen vacancies. Also, maximums were found which were formed by interstitial tin or tin with damaged bonds.
Analysis of the CVCs of SnO2-NWs/SiO2/Si heterostructures with orthorhombic crystal structure showed that SnO2-NWs/SiO2/Si heterostructures with arrays of p-n junctions were synthesized.
Our proposed template synthesis method has several advantages over other methods. Firstly, it does not require lithography. Secondly, it allows for quick optimization of the template synthesis process. Lastly, it has potential applicability to various material systems.

Author Contributions

Conceptualization, V.K. and A.I.P.; methodology, A.D. and V.K.; software, A.U. and A.-D.B.; validation, Z.B., D.J. and A.A. (Aiman Akylbekova); formal analysis, V.K., A.A. (Abdirash Akilbekov) and A.I.P.; investigation, Z.B., D.J., A.A. (Aiman Akylbekova), G.B., G.A. and A.U.; resources, A.A. (Abdirash Akilbekov), G.A. and A.-D.B.; data curation, D.J.; writing—original draft preparation, Z.B., A.D., D.J., G.B., A.U. and A.I.P.; writing—review and editing, A.D.; visualization, G.B.; supervision, A.D. and A.A. (Abdirash Akilbekov); project administration, G.A.; funding acquisition, A.D. All authors have read and agreed to the published version of the manuscript.

Funding

This research was funded by the Ministry of Science and Higher Education of the Republic of Kazakhstan, grant number AP14871479 «Template synthesis and experimental-theoretical study of a new type of heterostructures for nano- and optoelectronic applications».

Data Availability Statement

Data are contained within the article.

Acknowledgments

The work was carried out within the framework of the grant project AP14871479 of the Ministry of Science and Higher Education of the Republic of Kazakhstan.

Conflicts of Interest

The authors declare no conflicts of interest.

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Materials 17 01226 g001
Figure 1. SEM image of the n-type template surface after ECD at 1.75 V for 10 min.
Figure 1. SEM image of the n-type template surface after ECD at 1.75 V for 10 min.
Materials 17 01226 g001
Materials 17 01226 g002
Figure 2. X-ray diffractogram of samples obtained by the ECD for 10 min, at U = 1.75 V.
Figure 2. X-ray diffractogram of samples obtained by the ECD for 10 min, at U = 1.75 V.
Materials 17 01226 g002
Materials 17 01226 g003
Figure 3. Band structure and total density of states of pure SnO2 crystal. The green dotted lines mark the band edges that separate the 3.76 eV bandgap. The Fermi level corresponds to 0 eV.
Figure 3. Band structure and total density of states of pure SnO2 crystal. The green dotted lines mark the band edges that separate the 3.76 eV bandgap. The Fermi level corresponds to 0 eV.
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Materials 17 01226 g004
Figure 4. The SnO2 polymorph with ZrO2-type (Pbca) structure.
Figure 4. The SnO2 polymorph with ZrO2-type (Pbca) structure.
Materials 17 01226 g004
Materials 17 01226 g005
Figure 5. The photoluminescence spectrum of SnO2-NWs/SiO2/Si structures is decomposed into Gaussian components; SiO2 luminescence is taken into account in the PL spectrum.
Figure 5. The photoluminescence spectrum of SnO2-NWs/SiO2/Si structures is decomposed into Gaussian components; SiO2 luminescence is taken into account in the PL spectrum.
Materials 17 01226 g005
Materials 17 01226 g006
Figure 6. (a) Preparation of orthorhombic SnO2 nanowires by ECD in SiO2/Si and (b) the cross-section of filled template.
Figure 6. (a) Preparation of orthorhombic SnO2 nanowires by ECD in SiO2/Si and (b) the cross-section of filled template.
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Materials 17 01226 g007
Figure 7. Current–voltage characteristics of SnO2-NWs/SiO2/Si: dashed curve—initial sample; solid curve—with precipitated SnO2 (tdeposition = 10 min).
Figure 7. Current–voltage characteristics of SnO2-NWs/SiO2/Si: dashed curve—initial sample; solid curve—with precipitated SnO2 (tdeposition = 10 min).
Materials 17 01226 g007
Table 1. Crystallographic characteristics of SnO2 nanowires in SiO2/Si (-p) track template according to XRD results. The calculated parameters are presented in parentheses.
Table 1. Crystallographic characteristics of SnO2 nanowires in SiO2/Si (-p) track template according to XRD results. The calculated parameters are presented in parentheses.
Phase NameStructure TypeSpace Group(hkl)2θd, ÅL, nmFWHMCell Parameters, ÅVolume, Å3Density, g/cm3Degree of Crystallinity, %Phase Content, %
SnO2OrthorhombicPbca (61)20240.2192.2404619.390.485a = 9.97195
(10.05)
b = 5.11601
(5.10)
c = 5.03283
(5.18)		256.76
(266.26)		7.819
(7.57)		41.8100
Table 2. Parameters of intercrystalline barriers in SnO2 nanocrystallites.
Table 2. Parameters of intercrystalline barriers in SnO2 nanocrystallites.
H, nmT, Kmhk, ÅBarrier Height E, eV
70030010446.73.82 × 10−2
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Baimukhanov, Z.; Dauletbekova, A.; Junisbekova, D.; Kalytka, V.; Akilbekov, A.; Akylbekova, A.; Baubekova, G.; Aralbayeva, G.; Bazarbek, A.-D.; Usseinov, A.; et al. Synthesis of Orthorhombic Tin Dioxide Nanowires in Track Templates. Materials 2024, 17, 1226. https://doi.org/10.3390/ma17061226

AMA Style

Baimukhanov Z, Dauletbekova A, Junisbekova D, Kalytka V, Akilbekov A, Akylbekova A, Baubekova G, Aralbayeva G, Bazarbek A-D, Usseinov A, et al. Synthesis of Orthorhombic Tin Dioxide Nanowires in Track Templates. Materials. 2024; 17(6):1226. https://doi.org/10.3390/ma17061226

Chicago/Turabian Style

Baimukhanov, Zein, Alma Dauletbekova, Diana Junisbekova, Valeriy Kalytka, Abdirash Akilbekov, Aiman Akylbekova, Guldar Baubekova, Gulnara Aralbayeva, Assyl-Dastan Bazarbek, Abay Usseinov, and et al. 2024. "Synthesis of Orthorhombic Tin Dioxide Nanowires in Track Templates" Materials 17, no. 6: 1226. https://doi.org/10.3390/ma17061226

APA Style

Baimukhanov, Z., Dauletbekova, A., Junisbekova, D., Kalytka, V., Akilbekov, A., Akylbekova, A., Baubekova, G., Aralbayeva, G., Bazarbek, A.-D., Usseinov, A., & Popov, A. I. (2024). Synthesis of Orthorhombic Tin Dioxide Nanowires in Track Templates. Materials, 17(6), 1226. https://doi.org/10.3390/ma17061226

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