# GISAXS/GIXRD View of ZnO Films with Hierarchical Structural Elements

Authors: M. Lučić Lavčević; S. Bernstorff; P. Dubček; D. Jozić; I. Jerković; Z. Marijanović
Journal: Journal of Nanotechnology
 (2012)

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## Abstract

ZnO films constituted of porous sheet-like structures, formed by calcination of precursor, were examined using scanning electron microscopy and simultaneous small-angle scattering and diffraction of the synchrotron-sourced X-rays, under the grazing-incidence conditions. The presented analysis enabled insight into the complexity of the film morphology, which revealed substrate sensitivity on the microscopic and nanoscopic length scales. The average size and spatial arrangement of nanoparticles, single-crystal domains, and the average size and features of nanopores in sheet-like structures were determined for films deposited on glass, polycrystalline ZnO layer, and silicon.


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## Body

## 1. Introduction

Among the materials with dimensions in the range of microns to nanometers, a variety of ZnO structures have become the subject of numerous researches [1–3]. Generally, ZnO is a II-VI semiconductor and its features include good transparency, high electron mobility, and wide bandgap. For the use in various devices, it is typically fabricated in the form of thin film [4–7]. It is well known that functional properties of ZnO films depend on morphologies. For instance, films with different crystalline orientations exhibit different electronic and optical properties. Due to application requirements, it is therefore necessary to fine-tune the morphology of the film and characterize it in detail.In this paper we focus on ZnO films, with hierarchical structural elements builtin, including sheet-like structures, their constituents—nanoparticles, and the spatial arrangement of sheet-like structures and nanoparticles. The porous architecture of such films makes them suitable for application in optoelectronic and sensing devices, as well as in solar cells [8].There are several reactions and techniques for generating sheet-like ZnO structures [9–11]. Among them, the highly selective is the procedure of hydrothermal synthesis and thermal decomposition of a layered precursor of zinc hydroxide carbonate [11]. It was already investigated how the choice of starting chemicals, concentration, temperature, and pH affect the appearance, size, and arrangement of sheet-like structures in films [8, 11]. Determination of their morphology was mainly based on electron microscopy (EM), X-ray diffraction (XRD), and measurements based on nitrogen adsorption (BET). Along with characterization of films by common (EM and XRD) techniques, we here present and test the possibilities of a specific method for the analysis of sheet-like structures in ZnO films, which were formed via a selected procedure on substrates of different types.The analysis is based on the simultaneous grazing incidence small-angle X-ray scattering and grazing incidence X-ray diffraction (GISAXS/GIXRD) measurements, performed by using synchrotron radiation. GISAXS and GIXRD are nondestructive techniques, especially suitable for characterization of thin films and nanosized objects [12–15]. Instead of a localised information of the nanostructure, they provide averages across the irradiated area of the sample. The advantage of simultaneous measurements is based on the complementarity of the two techniques that probe the structural properties on different scales [16]. It is shown that the comparative GISAXS/GIXRD analysis of investigated ZnO films can provide a notable insight into the complex morphology, which evolves in sheet-like structures upon calcination of the precursor.The morphological characteristics of analyzed films showed significant substrate sensitivity. Therefore, their comprehensive description on the microscale and the nanoscale may be of applied interest, while combining films with different substrates in functional devices.


## 2. Experimental

### 2.1. Preparation Route

Three samples of ZnO films were prepared: sample A on a bare glass substrate, sample B on a ZnO-coated glass substrate, and sample C on a single-crystal Si (100) wafer substrate. ZnO coating for sample B was obtained by electron-beam evaporation technique, as a 200 nm thick polycrystalline layer on the glass substrate.Films were simultaneously grown on substrates, under the identical condition, following a well-known procedure [8, 11]. First, template films of Zn4CO3(OH)6·H2O were deposited from the solution of zinc nitrate hexahydrate and urea in deionized water, in concentrations of 0.05 M and 1.0 M, respectively. The pH value was adjusted to 4 by adding nitric acid to the solution. The substrates were immersed in three bottles with solution and heated in oven at 80°C for 6 hours. Finally, the calcination of dried templated films was performed in air at 300°C, transforming them into ZnO films.


### 2.2. Characterization

The insight in general morphologies of the synthesized films was realized in real space, by field emission scanning electron microscopy (FE-SEM Jeol 7000F).The analysis of nanosized ZnO particles/crystallites is based on the simultaneous GISAXS/GIXRD measurements. Scattering experiments were performed at the Austrian SAXS beamline at the Synchrotron Elettra (Trieste, Italy) [17]. A photon energy of 8 keV (λ=0.155 nm) was used, and the beam size was 4 mm × 0.150 mm (horizontal × vertical). The measurements were performed at a grazing-incident angle, larger than the so-called critical angle for total external reflection, at which X-rays penetrate the sample. The critical angle (around 0,37°) was determined experimentally for each film [18]. In the used setup for GISAXS/GIXRD measurements, samples were mounted on a stepping-motor-controlled tilting stage with a step resolution of 0.001°. At first, the stage (and the sample surface) was aligned horizontally and parallel to the incoming beam within ±0.1°. The configuration for GISAXS and GIXRD measurement is illustrated in Figure 1.Figure 1
The geometry of GISAXS/GIXRD measurements:αi and αf are the incident and the exit angle of the X-ray beam, respectively; ψ is the scattering in-plane angle; QH and QV are the horizontal and the vertical scattering vector, respectively; 2θ is the diffraction angle.The GISAXS patterns were recorded by a two dimensional charge coupled device (2D CCD) detector, containing 1024 × 1024 pixels and positioned perpendicular to the incident beam. A thin Al strip was placed in front of the detector to avoid its overflow.Two main directions, horizontal (parallel to the sample plane) and vertical (perpendicular to the sample plane), are represented by the position vectors in reciprocal space, the scattering vectorsQH and QV, respectively. Their moduli are defined by the wavelength λ, the incidence and exit angles αi and αf, and the in-plane scattering angle 2ψ of X-rays as
(1)QH=2πλ-1cosαfsinψ,QV=2πλ-1(sinαi+sinαf).The GIXRD measurements were performed simultaneously in the reflectivity plain, using a position sensitive detector (PSD), which covered an angular range (2θ) from 20° to 50°. Phase identification was realized matching diffracted peaks with PDF cards.The GISAXS/GIXRD patterns were corrected for readout noise and detector response.Conventional XRD measurements (in Bragg-Brentano geometry) were performed on samples using Philips X′pert diffractometer.


## 2.1. Preparation Route

Three samples of ZnO films were prepared: sample A on a bare glass substrate, sample B on a ZnO-coated glass substrate, and sample C on a single-crystal Si (100) wafer substrate. ZnO coating for sample B was obtained by electron-beam evaporation technique, as a 200 nm thick polycrystalline layer on the glass substrate.Films were simultaneously grown on substrates, under the identical condition, following a well-known procedure [8, 11]. First, template films of Zn4CO3(OH)6·H2O were deposited from the solution of zinc nitrate hexahydrate and urea in deionized water, in concentrations of 0.05 M and 1.0 M, respectively. The pH value was adjusted to 4 by adding nitric acid to the solution. The substrates were immersed in three bottles with solution and heated in oven at 80°C for 6 hours. Finally, the calcination of dried templated films was performed in air at 300°C, transforming them into ZnO films.


## 2.2. Characterization

The insight in general morphologies of the synthesized films was realized in real space, by field emission scanning electron microscopy (FE-SEM Jeol 7000F).The analysis of nanosized ZnO particles/crystallites is based on the simultaneous GISAXS/GIXRD measurements. Scattering experiments were performed at the Austrian SAXS beamline at the Synchrotron Elettra (Trieste, Italy) [17]. A photon energy of 8 keV (λ=0.155 nm) was used, and the beam size was 4 mm × 0.150 mm (horizontal × vertical). The measurements were performed at a grazing-incident angle, larger than the so-called critical angle for total external reflection, at which X-rays penetrate the sample. The critical angle (around 0,37°) was determined experimentally for each film [18]. In the used setup for GISAXS/GIXRD measurements, samples were mounted on a stepping-motor-controlled tilting stage with a step resolution of 0.001°. At first, the stage (and the sample surface) was aligned horizontally and parallel to the incoming beam within ±0.1°. The configuration for GISAXS and GIXRD measurement is illustrated in Figure 1.Figure 1
The geometry of GISAXS/GIXRD measurements:αi and αf are the incident and the exit angle of the X-ray beam, respectively; ψ is the scattering in-plane angle; QH and QV are the horizontal and the vertical scattering vector, respectively; 2θ is the diffraction angle.The GISAXS patterns were recorded by a two dimensional charge coupled device (2D CCD) detector, containing 1024 × 1024 pixels and positioned perpendicular to the incident beam. A thin Al strip was placed in front of the detector to avoid its overflow.Two main directions, horizontal (parallel to the sample plane) and vertical (perpendicular to the sample plane), are represented by the position vectors in reciprocal space, the scattering vectorsQH and QV, respectively. Their moduli are defined by the wavelength λ, the incidence and exit angles αi and αf, and the in-plane scattering angle 2ψ of X-rays as
(1)QH=2πλ-1cosαfsinψ,QV=2πλ-1(sinαi+sinαf).The GIXRD measurements were performed simultaneously in the reflectivity plain, using a position sensitive detector (PSD), which covered an angular range (2θ) from 20° to 50°. Phase identification was realized matching diffracted peaks with PDF cards.The GISAXS/GIXRD patterns were corrected for readout noise and detector response.Conventional XRD measurements (in Bragg-Brentano geometry) were performed on samples using Philips X′pert diffractometer.


## 3. Results and Discussion

### 3.1. FESEM View of the General Microscopic and Nanoscopic Morphology

The general morphologies of the samples A, B, and C, analyzed by FE-SEM, are shown in Figures2(a), 2(b), and 2(c). The FE-SEM images clearly exhibit that substrates are covered by nanostructures, which generally possess sheet-like morphologies. Sheets are about few micrometers in dimension and about 60 nm in thickness. The nanosized thickness classifies them as nanosheets. However, there are differences in both microscopic and nanoscopic morphology between samples A, B, and C obtained on amorphous (glass), polycrystalline (ZnO), and single crystal (Si) substrates, respectively.FE-SEM pictures of sample A (a), sample B (b), and sample C (c).
(a)
(b)
(c)In samples A and B nanosheets are self-organized as nanopetals, forming flower-like structures. In case of sample A, such flowers are about 5μm in dimension and show diversity in shape: mostly they are bush-like with randomly oriented petals or sprouts, assembled in a radiative way; otherwise, they adopt a shape of flowers in full blow. In sample B, flowers are bigger, about 8 μm in dimension; they have mostly regular form of rose-like flowers, with petals forming hollow central parts. Because of the specific spatial arrangement of nanopetals, the films are porous systems. Furthermore, a nanoscopic FE-SEM view reveals the inner porosity of the petals themselves: in both samples they are formed as networks of more or less agglomerated nanosized particles and nanopores (Figures 3(a) and 3(b)).FE-SEM pictures—nanoscopic view—of sample A (a), sample B (b), and sample C (c).
(a)
(b)
(c)In case of sample C, sheet-like nanostructures are not self-organized in flowers. They appear as individual truncated nanoleaves. Also, they are composed in a different manner, their nanoscopic FE-SEM image (Figure3(c)) exhibits a less porous structure.Evidently, the analysis by FE-SEM shows that the morphology of ZnO films is substrate dependent.The microdimensional constituents (flowers and leaves) of ZnO films, shown in Figure2, were obtained via a two-step synthesis, specified in Section 2. In the first step, template films consisting of microdimensional structures of Zn4CO3(OH)6·H2O were formed. In the second step, during the calcination, template films were transformed into ZnO films. According to the literature, final films preserve almost identical microscopic morphology (size and shape of flowers and leaves) as those obtained in the first step. Therefore Zn4CO3(OH)6·H2O acts as a self-template precursor and the final film morphology reflects the manner of growth of its layered structure. Under this assumption, we can conclude that the observed substrate dependence of the microscopic morphology of the films originates from the mechanism of the nucleation and growth of the Zn4CO3(OH)6·H2O on different substrates. The precursor nuclei are formed on the substrate surface by heterogeneous nucleation. There is no growth hindrance in the azimuthal direction until the growing sheets come into contact with each other. Then the self-assembled microstructures of the precursor nanosheets are generally made, like flowers in samples A and B. From the thermodynamics point of view, nanosheets tend to aggregate to decrease the surface energy by reducing exposed areas; besides, the interaction between the deposit material and the substrate surface must be taken into account. The number and type of nucleation sites basically depend on the substrate characteristics, such as roughness, chemical composition, and crystallographic structure. Furthermore, the hydrophilic/hydrophobic interactions between the growing sheets and the substrate can affect the manner of the film growth. Although the assembling of nanosheets in flower-like structures takes place in samples A and B, forming the same general morphology in both samples, flowers grown on polycrystalline ZnO substrate have more regular shape and sheet distribution than those grown on amorphous glass surface. One of the possible reasons may be a certain degree of similarity between the structure of the substrate and the precursor. Furthermore, the tendency of petals in sample A to direct themselves upwards, rather than to spread on the substrate, is probably caused by the difference in the hydrophobicity of the surface of Zn4CO3(OH)6·H2O and the surface of ZnO nanostructured substrate. Finally, the absence of the self-assembling of sheets in sample C can also be tentatively ascribed to hydrophobic interactions and geometric effects between the precursor and the single-crystal silicon surface.Differences between the as-prepared precursor and the final ZnO film are mostly related to the nanoscopic morphology of their structures and are caused by the formation of pores during the heating process.The formation of the porous network in a petal takes place during the conversion of theZn4CO3(OH)6 precursor to ZnO at 300°C, according to the following chemical reaction:
(2)Zn4CO3(OH)6H2O+O2→4ZnO+4H2O+CO2During the thermal process, besides smallZnO units, vacancies are formed that balance the released molecules H2O and CO2. The nanosized pores in the sheets might come from the effect, in which the vacancies formed in the initial period condense to form voids. Additionally, after the initial period and with increasing temperature, ZnO units assemble into nanoparticles.In summary, the FE-SEM view suggests that the morphology of films exhibits substrate sensitivity and can be considered in the frame of four hierarchical elements: single sheet, single nanoparticle, spatial arrangement of the sheets, and spatial arrangement of nanoparticles.GIXRD and GISAXS enable an insight in this complex morphology on the nanoscopic level.


### 3.2. GIXRD View of the Nanoscopic Morphology and Crystallographic Structure

From GIXRD patterns, shown in Figures4(a), 4(b), and 4(c), the crystallographic structure of the samples was examined. The recorded diffraction peaks match with crystalline hexagonal wurtzite-type structure and correspond to (100), (002), and (101) planes of ZnO, respectively.GIXRD patterns of sample A (a), sample B (b), and sample C (c).
(a)
(b)
(c)The relative intensities of the peaks in the GIXRD patterns differ among the samples, indicating different degrees of crystallographic orientation in films. GIXRD can not be used for a straightforward interpretation of the intensity scans considering the preferred orientations: as the incident angle is fixed, the scan normal varies with the diffraction angle. Therefore, each diffraction peak in a grazing incidence pattern corresponds to a different orientation of the reflecting planes. Since the geometry of measurements is not symmetrical, some reflections can be hindered. For an accurate estimate of the texture, conventional XRD measurements on samples (shown later in text) are needed. However, some assumptions about orientation can be made using GIXRD. As shown in Figure4, all dominant peaks appear in the GIXRD patterns of samples A and B, indicating that the single crystal domains in these samples are either randomly oriented or eventually weakly ordered. On the other hand, the pattern of sample C exhibits a dominant contribution of the (100) and (101) peaks and a barely resoluble (002) peak. Such pattern, recorded in the grazing incidence mode, suggests that a significant portion of single crystal domains in this sample is oriented with their c-axis parallel to the film surface, since the tilt between the (100) plane and the scan normal is close to 90° for the given grazing incident angle.The broadening of diffraction peaks reveals that the size of single crystal domains is in the nanometer range, that is, they are nanocrystals. The average size was calculated from the profile width at half maximum height of the given peaks, using the following Scherrer equation [19]:
(3)L(hkl)=Kλβcosθ,
where L(hkl) is the average nanocrystal size (which may be smaller or equal to the particle size) estimated from the (hkl) reflection, λ (=0.1554 nm) is the wavelength of synchrotron sourced X-rays, β is the broadening of diffraction line measured at half its maximum intensity in radians, and θ is the angular peak position. According to the widespread practice, a value of one was retained for Scherrer constant K. Generally, the Scherrer constant depends on the crystallite shape and on the size distribution. However, it is not a bad approximation in this case, if, for each (hkl) reflection, the crystallite size L is interpreted as an average crystal dimension perpendicular to the corresponding reflecting plane. The average nanocrystal sizes in samples A, B, and C were calculated from the dominant peaks of ZnO. The instrumental broadening of 0.2° was incorporated in the size calculations.The estimated sizes, much smaller than any dimension of the sheets, complement the microscopic picture showing that sheets exhibit polycrystalline structure.The average nanocrystal sizes in samples A and B are similar, with the exception of one enhanced size, estimated from the (002) peak in the pattern of sample B. The average crystallite sizes in sample C are slightly lower and can be properly estimated only for the (100) and (101) reflections. Similar nanocrystal sizes, estimated from different peaks of the sample A, suggest that it consists of isotropically shaped or randomly oriented nanocrystals. The (002) peak of sample B, sharper than others and stronger than that of standard pattern, indicates that nanocrystals have anisotropic shape, elongated in the direction of the c-axis.According to the FE-SEM pictures, the average size of single nanoparticles, agglomerated in petals, correlate well with the estimated average size of nanocrystals. We can conclude that most of the single nanoparticles in petals are single crystal domains. This conclusion does not apply to particles forming leaves, as their size cannot be properly estimated by FE-SEM.


### 3.3. GISAXS View of the Nanoscopic Morphology

The FE-SEM analysis allow us to consider petals and leaves in ZnO films as two-phased systems, composed of nanosized particles and pores. As the SAXS signal arises from the difference in electron density between the two phases, it is suitable for the analysis of the porous samples. Their 2D GISAXS patterns, given in Figure5, represent the maps of scattered intensities in the given in-plane and out-of-plane angular scattering ranges. The maximum of the scattered intensity is in the direction of the specular plane (QH=0), which is normal to the surface of the sample. This scattered intensity is partly reduced by a thin Al absorber (vertical strips in the patterns are depleted intensities). The lower part of the scattering is missing because of the absorption in the sample. For exit angles equal to incident critical angle (αf=αc), there is an enhancement in the scattering intensity due to the refraction effects, which is also known as Yoneda peak. The presence of small angle X-ray scattering in patterns indicates the existence of nanosized heterogeneities in electron density in all samples. 2D GISAXS patterns allow determination of dimensions of the scattering objects along horizontal and vertical direction, represented by the scattering vectors QH and QV, respectively. The method of interpreting scattering data is based on the analysis of the intensity cuts, which show the dependence of the intensity, I, on the scattering vector, Qi(QHorQV). The intensity cuts, that is, one dimensional scattering curves, taken from Figure 5 at fixed values of horizontal and vertical scattering vectors (relatively close to the Yoneda peak and to the specular plane), were used to calculate the so-called Guinier radii, RGV and RGH, which give information about the average size in given directions.2D GISAXS patterns of sample A (a), sample B (b), and sample C (c).
(a)
(b)
(c)The white strips indicate where the intensity cut shown in Figures6 and 7 was taken.Figure 6
Scattering curves of sample B, extracted from Figure5(b) as vertical cut at a constant value of the horizontal wave vector (red) and horizontal cut at a constant value of the vertical wave vector (green), shown in the presentation suitable for determination of the average gyration radius. β is the slope of the fitting lines (black).Figure 7
The Porod graph, obtained from the vertical intensity cut of sample B (shown in Figure5(b)); n is the slope of the fitting line (red).In the Guinier approximation [20], scattering in the small Q-region depends only on the overall size of the object and not on its shape, so the scattered intensity I(Q) can be expressed as
(4)I(Q)=CGexp(-RG2Q23).The Guinier radiusRG is the average radius of gyration of a dilute set of randomly oriented scattering centers. When this condition is not fulfilled, it still can be calculated as a rough approximation. In order to determine the gyration radii, we used the so-called Guinier graph: we plotted the intensity cuts in the LnI versus Qi2 presentation and fitted each of them by a line for very small scattering vectors. As example, the fitting of a vertical and a horizontal cut is represented in Figure 6 for sample B. The two white strips in Figure 5(b) indicate where the 1D cut shown in Figure 6 was taken.For a slopeβ of the fitting line, the corresponding Guinier radius is calculated as
(5)RG=(-3β)1/2.
The determined gyration radii RGH and RGV for the samples A, B, and C are shown in Table 2.The Guinier radii for sample B obtained from a horizontal and a vertical intensity scan have similar values, which suggest that scattering objects are either spherical or anisotropic forms with random orientation. The average diameter,D, for a sphere can be calculated from the following average gyration radius:
(6)D=2RG53.The resulting average diameter of 8.8 nm does not correspond to the average crystallite size in this sample (Table1). As crystallites can not be bigger than particles, this result reveals that scattering objects in sample B are not particles, but nanosized pores inside the petals. The same conclusion applies to sample A, although in this sample the radii of gyration differ in the two directions, suggesting the slight anisotropy of pores. Anisotropy in SAXS results from more or less oriented scattering objects. Although Guinier approximation gives only the radius as a measure of size, it is also partly sensitive to oriented flat or elongated scattering objects. The analysis of vertical and horizontal scans of sample C showed the significant difference in the corresponding average gyration radii (RGH/RGV=1.9). Therefore, the anisotropy of scattering objects (also evident from the shape of the 2D GISAXS pattern in Figure 5(c)) is assumed. It can be related to the anisotropy in crystallite orientations of this sample, shown by the GIWAXS. The size of scattering objects, suggested by the value of the gyration radii, is comparable to the size of crystallites in this sample. However, considering the more dense structure of leaves in comparison to petals, the scattering can still be ascribed to pores.Table 1
The GIXRD data of the ZnO thin films: crystallite sizes,L(hkl), estimated from (100), (002), and (101) reflections.
Sample
L
(
100
)
/nm
L
(
002
)
/nm
L
(
101
)
/nm
A
13
14
12
B
14
17
13
C
12
/
11Table 2
The Guinier radii,RGH, and RGV for samples A, B, and C, calculated from vertical and horizontal intensity cuts.
Sample
R
G
H/nm
R
G
V/nm
A
3.1
3.5
B
3.3
3.4
C
4.2
2.2Besides the Guinier graph, the so-called Porod graph can be exploited for the further analysis of scattering. In the Porod approximation for a two-phase system [21], the scattering radiation in the high Q-region is probing the local structure. For this analysis, the intensity cuts from Figure 5 were plotted in the LnI versus LnQi presentation and fitted by a line for high scattering vectors. The slope n of the fitting line yields information about the so-called “fractal dimension” of the scattering objects. As example, the Porod graph obtained from the intensity cut of the sample B (Figure 5(b)) is shown in Figure 7.The Porod slopes estimated for samples A, B, and C, as the two-phased systems of particles and pores, are −3.1, −3.3, and −4, respectively. The slopes determined for samples A and B represent rough interfaces between particles and pores, while slope −4 indicates a smooth interface in sample C. Again, the exceptional behavior of morphological characteristics of this sample is confirmed. Leaves, as its structure elements, exhibit not only the lack of self-organizing, but also a different inner structure: while evolving in leaves, the constituent ZnO units are stacked into anisotropic forms with smooth surfaces, arranged more densely than those in petals. As compared to the other two samples, the more pronounced Yoneda peak in the scattering pattern of sample C additionally confirms the more smoothed surface.In order to verify the GISAXS/GIXRD view of samples and enhance the information on their structural properties, the samples were finally investigated by XRD in Bragg-Brentano geometry.


### 3.4. Conventional XRD Measurements

Conventional XRD measurements enable determination of reflections from the crystal planes which are parallel to the sample surface. XRD patterns of samples A, B, and C, shown in Figure8, were recorded in a wider angular range in comparison to that used in the GIXRD measurements. Therefore, two additional peaks are visible, which correspond to (102) and (110) reflecting planes. The contribution of the amorphous glass substrate is evident for samples A and B.XRD patterns of sample A (a), sample B (b), and sample C (c).
(a)
(b)
(c)Average nanocrystal sizes,L(hkl), estimated using (3) from the dominant (100), (002), and (101) reflections, are given in Table 3. Crystallite sizes obtained from conventional XRD correlate well with those obtained from GIXRD. Taking into account that XRD data refer to the entire sample, while those of GIXRD describe only its upper part, we can conclude that the petals and leaves have uniform inner structure on the whole.Table 3
Average nanocrystal sizes,L(hkl), estimated from (100), (002), and (101) reflections, from conventional XRD measurements.
Sample
L
(
100
)
/nm
L
(
002
)
/nm
L
(
101
)
/nm
A
12
12
11
B
14
18
14
C
13
/
11As in the case of GIXRD patterns, the relative intensities of the peaks in the XRD patterns differ among the samples. However, unlike GIXRD, conventional XRD can be used for a straightforward interpretation of the intensity scans considering the preferred orientations. The estimation of the film texture is generally based on the comparison of the orientation distribution of single crystal domains in film with entirely random orientation of domains in a powder sample, taken as standard. The texture of the particular plane can be presented by the texture coefficient [22], deviation of which from unity implies the preferential crystallite orientation. So, the texture coefficient T(hkl) is defined as
(7)T(hkl)=I(hkl)/I0(hkl)n-1∑n(I(hkl)/I0(hkl)),
where I(hkl) is the measured relative intensity of a plane (hkl),I0(hkl) is the standard intensity of the plane (hkl) taken from the JCPDS data, and n is the number of diffraction peaks. In the present analysis, n=5, because five directions are involved (100), (002), (101), (102), and (110). A sample with randomly oriented crystallite presents T(hkl)=1, while the larger this value, the larger the abundance of domains oriented at the (hkl) direction. The estimated texture coefficients (shown in Table 4) fit into the image of nanoscopic morphology, formed by this point.Table 4
Texture coefficients,T(hkl), estimated from (100), (002), (101), (102), and (110) reflections, from conventional XRD measurements.
Sample
T
(
100
)
T
(
002
)
T
(
101
)
T
(
102
)
T
(
110
)
A
1.1
1.2
0.9
1.1
0.8
B
1.0
1.5
0.7
1.0
0.8
C
1.8
0.6
0.9
0.7
1.0The values of the texture coefficient confirm the difference in the spatial orientation of nanocrystals between samples, indicated by GIXRD and probably caused by the substrate-induced difference on the microscale: the nanocrystals in petals of flowers on glass are randomly oriented, and those in petals of rose-like flowers on polycrystalline ZnO exhibit a weak (002) texture. Further, the portion of nanocrystals arranged with their c-axis perpendicular to the substrate is relatively small in leaves grown on silicon. A relatively pronounced (110) reflection in the XRD pattern of this sample confirms its previously presumed texture: besides a number of nanocrystals with c-axis tilted with respect to the substrate, which are partly represented by the (101) reflection, most of nanocrystals seem to be arranged with c-axis parallel to the sample surface. Such arrangement of nanocrystals is common to both orientations (100) and (110).


## 3.1. FESEM View of the General Microscopic and Nanoscopic Morphology

The general morphologies of the samples A, B, and C, analyzed by FE-SEM, are shown in Figures2(a), 2(b), and 2(c). The FE-SEM images clearly exhibit that substrates are covered by nanostructures, which generally possess sheet-like morphologies. Sheets are about few micrometers in dimension and about 60 nm in thickness. The nanosized thickness classifies them as nanosheets. However, there are differences in both microscopic and nanoscopic morphology between samples A, B, and C obtained on amorphous (glass), polycrystalline (ZnO), and single crystal (Si) substrates, respectively.FE-SEM pictures of sample A (a), sample B (b), and sample C (c).
(a)
(b)
(c)In samples A and B nanosheets are self-organized as nanopetals, forming flower-like structures. In case of sample A, such flowers are about 5μm in dimension and show diversity in shape: mostly they are bush-like with randomly oriented petals or sprouts, assembled in a radiative way; otherwise, they adopt a shape of flowers in full blow. In sample B, flowers are bigger, about 8 μm in dimension; they have mostly regular form of rose-like flowers, with petals forming hollow central parts. Because of the specific spatial arrangement of nanopetals, the films are porous systems. Furthermore, a nanoscopic FE-SEM view reveals the inner porosity of the petals themselves: in both samples they are formed as networks of more or less agglomerated nanosized particles and nanopores (Figures 3(a) and 3(b)).FE-SEM pictures—nanoscopic view—of sample A (a), sample B (b), and sample C (c).
(a)
(b)
(c)In case of sample C, sheet-like nanostructures are not self-organized in flowers. They appear as individual truncated nanoleaves. Also, they are composed in a different manner, their nanoscopic FE-SEM image (Figure3(c)) exhibits a less porous structure.Evidently, the analysis by FE-SEM shows that the morphology of ZnO films is substrate dependent.The microdimensional constituents (flowers and leaves) of ZnO films, shown in Figure2, were obtained via a two-step synthesis, specified in Section 2. In the first step, template films consisting of microdimensional structures of Zn4CO3(OH)6·H2O were formed. In the second step, during the calcination, template films were transformed into ZnO films. According to the literature, final films preserve almost identical microscopic morphology (size and shape of flowers and leaves) as those obtained in the first step. Therefore Zn4CO3(OH)6·H2O acts as a self-template precursor and the final film morphology reflects the manner of growth of its layered structure. Under this assumption, we can conclude that the observed substrate dependence of the microscopic morphology of the films originates from the mechanism of the nucleation and growth of the Zn4CO3(OH)6·H2O on different substrates. The precursor nuclei are formed on the substrate surface by heterogeneous nucleation. There is no growth hindrance in the azimuthal direction until the growing sheets come into contact with each other. Then the self-assembled microstructures of the precursor nanosheets are generally made, like flowers in samples A and B. From the thermodynamics point of view, nanosheets tend to aggregate to decrease the surface energy by reducing exposed areas; besides, the interaction between the deposit material and the substrate surface must be taken into account. The number and type of nucleation sites basically depend on the substrate characteristics, such as roughness, chemical composition, and crystallographic structure. Furthermore, the hydrophilic/hydrophobic interactions between the growing sheets and the substrate can affect the manner of the film growth. Although the assembling of nanosheets in flower-like structures takes place in samples A and B, forming the same general morphology in both samples, flowers grown on polycrystalline ZnO substrate have more regular shape and sheet distribution than those grown on amorphous glass surface. One of the possible reasons may be a certain degree of similarity between the structure of the substrate and the precursor. Furthermore, the tendency of petals in sample A to direct themselves upwards, rather than to spread on the substrate, is probably caused by the difference in the hydrophobicity of the surface of Zn4CO3(OH)6·H2O and the surface of ZnO nanostructured substrate. Finally, the absence of the self-assembling of sheets in sample C can also be tentatively ascribed to hydrophobic interactions and geometric effects between the precursor and the single-crystal silicon surface.Differences between the as-prepared precursor and the final ZnO film are mostly related to the nanoscopic morphology of their structures and are caused by the formation of pores during the heating process.The formation of the porous network in a petal takes place during the conversion of theZn4CO3(OH)6 precursor to ZnO at 300°C, according to the following chemical reaction:
(2)Zn4CO3(OH)6H2O+O2→4ZnO+4H2O+CO2During the thermal process, besides smallZnO units, vacancies are formed that balance the released molecules H2O and CO2. The nanosized pores in the sheets might come from the effect, in which the vacancies formed in the initial period condense to form voids. Additionally, after the initial period and with increasing temperature, ZnO units assemble into nanoparticles.In summary, the FE-SEM view suggests that the morphology of films exhibits substrate sensitivity and can be considered in the frame of four hierarchical elements: single sheet, single nanoparticle, spatial arrangement of the sheets, and spatial arrangement of nanoparticles.GIXRD and GISAXS enable an insight in this complex morphology on the nanoscopic level.


## 3.2. GIXRD View of the Nanoscopic Morphology and Crystallographic Structure

From GIXRD patterns, shown in Figures4(a), 4(b), and 4(c), the crystallographic structure of the samples was examined. The recorded diffraction peaks match with crystalline hexagonal wurtzite-type structure and correspond to (100), (002), and (101) planes of ZnO, respectively.GIXRD patterns of sample A (a), sample B (b), and sample C (c).
(a)
(b)
(c)The relative intensities of the peaks in the GIXRD patterns differ among the samples, indicating different degrees of crystallographic orientation in films. GIXRD can not be used for a straightforward interpretation of the intensity scans considering the preferred orientations: as the incident angle is fixed, the scan normal varies with the diffraction angle. Therefore, each diffraction peak in a grazing incidence pattern corresponds to a different orientation of the reflecting planes. Since the geometry of measurements is not symmetrical, some reflections can be hindered. For an accurate estimate of the texture, conventional XRD measurements on samples (shown later in text) are needed. However, some assumptions about orientation can be made using GIXRD. As shown in Figure4, all dominant peaks appear in the GIXRD patterns of samples A and B, indicating that the single crystal domains in these samples are either randomly oriented or eventually weakly ordered. On the other hand, the pattern of sample C exhibits a dominant contribution of the (100) and (101) peaks and a barely resoluble (002) peak. Such pattern, recorded in the grazing incidence mode, suggests that a significant portion of single crystal domains in this sample is oriented with their c-axis parallel to the film surface, since the tilt between the (100) plane and the scan normal is close to 90° for the given grazing incident angle.The broadening of diffraction peaks reveals that the size of single crystal domains is in the nanometer range, that is, they are nanocrystals. The average size was calculated from the profile width at half maximum height of the given peaks, using the following Scherrer equation [19]:
(3)L(hkl)=Kλβcosθ,
where L(hkl) is the average nanocrystal size (which may be smaller or equal to the particle size) estimated from the (hkl) reflection, λ (=0.1554 nm) is the wavelength of synchrotron sourced X-rays, β is the broadening of diffraction line measured at half its maximum intensity in radians, and θ is the angular peak position. According to the widespread practice, a value of one was retained for Scherrer constant K. Generally, the Scherrer constant depends on the crystallite shape and on the size distribution. However, it is not a bad approximation in this case, if, for each (hkl) reflection, the crystallite size L is interpreted as an average crystal dimension perpendicular to the corresponding reflecting plane. The average nanocrystal sizes in samples A, B, and C were calculated from the dominant peaks of ZnO. The instrumental broadening of 0.2° was incorporated in the size calculations.The estimated sizes, much smaller than any dimension of the sheets, complement the microscopic picture showing that sheets exhibit polycrystalline structure.The average nanocrystal sizes in samples A and B are similar, with the exception of one enhanced size, estimated from the (002) peak in the pattern of sample B. The average crystallite sizes in sample C are slightly lower and can be properly estimated only for the (100) and (101) reflections. Similar nanocrystal sizes, estimated from different peaks of the sample A, suggest that it consists of isotropically shaped or randomly oriented nanocrystals. The (002) peak of sample B, sharper than others and stronger than that of standard pattern, indicates that nanocrystals have anisotropic shape, elongated in the direction of the c-axis.According to the FE-SEM pictures, the average size of single nanoparticles, agglomerated in petals, correlate well with the estimated average size of nanocrystals. We can conclude that most of the single nanoparticles in petals are single crystal domains. This conclusion does not apply to particles forming leaves, as their size cannot be properly estimated by FE-SEM.


## 3.3. GISAXS View of the Nanoscopic Morphology

The FE-SEM analysis allow us to consider petals and leaves in ZnO films as two-phased systems, composed of nanosized particles and pores. As the SAXS signal arises from the difference in electron density between the two phases, it is suitable for the analysis of the porous samples. Their 2D GISAXS patterns, given in Figure5, represent the maps of scattered intensities in the given in-plane and out-of-plane angular scattering ranges. The maximum of the scattered intensity is in the direction of the specular plane (QH=0), which is normal to the surface of the sample. This scattered intensity is partly reduced by a thin Al absorber (vertical strips in the patterns are depleted intensities). The lower part of the scattering is missing because of the absorption in the sample. For exit angles equal to incident critical angle (αf=αc), there is an enhancement in the scattering intensity due to the refraction effects, which is also known as Yoneda peak. The presence of small angle X-ray scattering in patterns indicates the existence of nanosized heterogeneities in electron density in all samples. 2D GISAXS patterns allow determination of dimensions of the scattering objects along horizontal and vertical direction, represented by the scattering vectors QH and QV, respectively. The method of interpreting scattering data is based on the analysis of the intensity cuts, which show the dependence of the intensity, I, on the scattering vector, Qi(QHorQV). The intensity cuts, that is, one dimensional scattering curves, taken from Figure 5 at fixed values of horizontal and vertical scattering vectors (relatively close to the Yoneda peak and to the specular plane), were used to calculate the so-called Guinier radii, RGV and RGH, which give information about the average size in given directions.2D GISAXS patterns of sample A (a), sample B (b), and sample C (c).
(a)
(b)
(c)The white strips indicate where the intensity cut shown in Figures6 and 7 was taken.Figure 6
Scattering curves of sample B, extracted from Figure5(b) as vertical cut at a constant value of the horizontal wave vector (red) and horizontal cut at a constant value of the vertical wave vector (green), shown in the presentation suitable for determination of the average gyration radius. β is the slope of the fitting lines (black).Figure 7
The Porod graph, obtained from the vertical intensity cut of sample B (shown in Figure5(b)); n is the slope of the fitting line (red).In the Guinier approximation [20], scattering in the small Q-region depends only on the overall size of the object and not on its shape, so the scattered intensity I(Q) can be expressed as
(4)I(Q)=CGexp(-RG2Q23).The Guinier radiusRG is the average radius of gyration of a dilute set of randomly oriented scattering centers. When this condition is not fulfilled, it still can be calculated as a rough approximation. In order to determine the gyration radii, we used the so-called Guinier graph: we plotted the intensity cuts in the LnI versus Qi2 presentation and fitted each of them by a line for very small scattering vectors. As example, the fitting of a vertical and a horizontal cut is represented in Figure 6 for sample B. The two white strips in Figure 5(b) indicate where the 1D cut shown in Figure 6 was taken.For a slopeβ of the fitting line, the corresponding Guinier radius is calculated as
(5)RG=(-3β)1/2.
The determined gyration radii RGH and RGV for the samples A, B, and C are shown in Table 2.The Guinier radii for sample B obtained from a horizontal and a vertical intensity scan have similar values, which suggest that scattering objects are either spherical or anisotropic forms with random orientation. The average diameter,D, for a sphere can be calculated from the following average gyration radius:
(6)D=2RG53.The resulting average diameter of 8.8 nm does not correspond to the average crystallite size in this sample (Table1). As crystallites can not be bigger than particles, this result reveals that scattering objects in sample B are not particles, but nanosized pores inside the petals. The same conclusion applies to sample A, although in this sample the radii of gyration differ in the two directions, suggesting the slight anisotropy of pores. Anisotropy in SAXS results from more or less oriented scattering objects. Although Guinier approximation gives only the radius as a measure of size, it is also partly sensitive to oriented flat or elongated scattering objects. The analysis of vertical and horizontal scans of sample C showed the significant difference in the corresponding average gyration radii (RGH/RGV=1.9). Therefore, the anisotropy of scattering objects (also evident from the shape of the 2D GISAXS pattern in Figure 5(c)) is assumed. It can be related to the anisotropy in crystallite orientations of this sample, shown by the GIWAXS. The size of scattering objects, suggested by the value of the gyration radii, is comparable to the size of crystallites in this sample. However, considering the more dense structure of leaves in comparison to petals, the scattering can still be ascribed to pores.Table 1
The GIXRD data of the ZnO thin films: crystallite sizes,L(hkl), estimated from (100), (002), and (101) reflections.
Sample
L
(
100
)
/nm
L
(
002
)
/nm
L
(
101
)
/nm
A
13
14
12
B
14
17
13
C
12
/
11Table 2
The Guinier radii,RGH, and RGV for samples A, B, and C, calculated from vertical and horizontal intensity cuts.
Sample
R
G
H/nm
R
G
V/nm
A
3.1
3.5
B
3.3
3.4
C
4.2
2.2Besides the Guinier graph, the so-called Porod graph can be exploited for the further analysis of scattering. In the Porod approximation for a two-phase system [21], the scattering radiation in the high Q-region is probing the local structure. For this analysis, the intensity cuts from Figure 5 were plotted in the LnI versus LnQi presentation and fitted by a line for high scattering vectors. The slope n of the fitting line yields information about the so-called “fractal dimension” of the scattering objects. As example, the Porod graph obtained from the intensity cut of the sample B (Figure 5(b)) is shown in Figure 7.The Porod slopes estimated for samples A, B, and C, as the two-phased systems of particles and pores, are −3.1, −3.3, and −4, respectively. The slopes determined for samples A and B represent rough interfaces between particles and pores, while slope −4 indicates a smooth interface in sample C. Again, the exceptional behavior of morphological characteristics of this sample is confirmed. Leaves, as its structure elements, exhibit not only the lack of self-organizing, but also a different inner structure: while evolving in leaves, the constituent ZnO units are stacked into anisotropic forms with smooth surfaces, arranged more densely than those in petals. As compared to the other two samples, the more pronounced Yoneda peak in the scattering pattern of sample C additionally confirms the more smoothed surface.In order to verify the GISAXS/GIXRD view of samples and enhance the information on their structural properties, the samples were finally investigated by XRD in Bragg-Brentano geometry.


## 3.4. Conventional XRD Measurements

Conventional XRD measurements enable determination of reflections from the crystal planes which are parallel to the sample surface. XRD patterns of samples A, B, and C, shown in Figure8, were recorded in a wider angular range in comparison to that used in the GIXRD measurements. Therefore, two additional peaks are visible, which correspond to (102) and (110) reflecting planes. The contribution of the amorphous glass substrate is evident for samples A and B.XRD patterns of sample A (a), sample B (b), and sample C (c).
(a)
(b)
(c)Average nanocrystal sizes,L(hkl), estimated using (3) from the dominant (100), (002), and (101) reflections, are given in Table 3. Crystallite sizes obtained from conventional XRD correlate well with those obtained from GIXRD. Taking into account that XRD data refer to the entire sample, while those of GIXRD describe only its upper part, we can conclude that the petals and leaves have uniform inner structure on the whole.Table 3
Average nanocrystal sizes,L(hkl), estimated from (100), (002), and (101) reflections, from conventional XRD measurements.
Sample
L
(
100
)
/nm
L
(
002
)
/nm
L
(
101
)
/nm
A
12
12
11
B
14
18
14
C
13
/
11As in the case of GIXRD patterns, the relative intensities of the peaks in the XRD patterns differ among the samples. However, unlike GIXRD, conventional XRD can be used for a straightforward interpretation of the intensity scans considering the preferred orientations. The estimation of the film texture is generally based on the comparison of the orientation distribution of single crystal domains in film with entirely random orientation of domains in a powder sample, taken as standard. The texture of the particular plane can be presented by the texture coefficient [22], deviation of which from unity implies the preferential crystallite orientation. So, the texture coefficient T(hkl) is defined as
(7)T(hkl)=I(hkl)/I0(hkl)n-1∑n(I(hkl)/I0(hkl)),
where I(hkl) is the measured relative intensity of a plane (hkl),I0(hkl) is the standard intensity of the plane (hkl) taken from the JCPDS data, and n is the number of diffraction peaks. In the present analysis, n=5, because five directions are involved (100), (002), (101), (102), and (110). A sample with randomly oriented crystallite presents T(hkl)=1, while the larger this value, the larger the abundance of domains oriented at the (hkl) direction. The estimated texture coefficients (shown in Table 4) fit into the image of nanoscopic morphology, formed by this point.Table 4
Texture coefficients,T(hkl), estimated from (100), (002), (101), (102), and (110) reflections, from conventional XRD measurements.
Sample
T
(
100
)
T
(
002
)
T
(
101
)
T
(
102
)
T
(
110
)
A
1.1
1.2
0.9
1.1
0.8
B
1.0
1.5
0.7
1.0
0.8
C
1.8
0.6
0.9
0.7
1.0The values of the texture coefficient confirm the difference in the spatial orientation of nanocrystals between samples, indicated by GIXRD and probably caused by the substrate-induced difference on the microscale: the nanocrystals in petals of flowers on glass are randomly oriented, and those in petals of rose-like flowers on polycrystalline ZnO exhibit a weak (002) texture. Further, the portion of nanocrystals arranged with their c-axis perpendicular to the substrate is relatively small in leaves grown on silicon. A relatively pronounced (110) reflection in the XRD pattern of this sample confirms its previously presumed texture: besides a number of nanocrystals with c-axis tilted with respect to the substrate, which are partly represented by the (101) reflection, most of nanocrystals seem to be arranged with c-axis parallel to the sample surface. Such arrangement of nanocrystals is common to both orientations (100) and (110).


## 4. Conclusion

In summary, we generated nanostructured ZnO films with hierarchical structural elements, via hydrothermal synthesis and thermal decomposition of the zinc hydroxide carbonate as precursor, using different substrates. The FE-SEM measurements showed that the nature of substrate has a strong influence on the hierarchical elements (nanosheets and their spatial arrangement) on the microscale. By the combined GISAXS/GIXRD method of analysis, it was elucidated how this substrate sensitivity reflects on the morphology on the nanoscale. The average size and shape of the constituents of nanosheets, nanocrystals/nanoparticles, and nanopores, as well as the nature of the inner surface of the sheets, were estimated for samples on different substrates. The development of different crystallographic orientations of nanocrystals in samples, indicated by GIXRD, was confirmed and defined in detail by XRD. It was found that their orientation is probably ruled by the spatial arrangement of sheets (i.e., by the hierarchical characteristics on the microscale).However, the texture of sample B, which exhibits a weak out-of-plane ordering related to increased number of nanocrystals with their c-axis perpendicular to the substrate, should be additionally commented. Namely, the substrate in this sample is a 200 nm thick polycrystalline layer of ZnO, with single crystal domains of average size of 20 nm. The conventional XRD of this layer shows hardly resoluble ZnO peaks because of the glass absorption, while its GIXRD pattern correlate with that of sample B. This indicates that orientation of nanocrystals may not depend solely on the spatial arrangement of the sheets, but is partly conditioned by the substrate. Further investigations of films deposited on various textured layers should clarify whether the substrate affects the mutual arrangement of nanocrystals/nanoparticles in sheets.In conclusion, the combined GISAXS/GIXRD method was successful in estimation of the substrate-induced changes in morphology on the nanoscale. Along with FE-SEM, this method allows a comprehensive assessment of the morphological characteristics, which define the properties of film in application. The determined film characteristics can be tuned to be useful in dye-sensitized solar cells (for the enhancement of dye absorption, electrolyte distribution, and electrical pathways via nanoporosity, large surface area, and orientation of nanocrystals), in sensing devices (for the enhanced gas sensing through the enlargement of density in vacancies of the porous sheets) and as catalysts (for the enhancement of activity due to good crystallinity and large surface area).



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*Source: 354809-2012-12-20.xml*