ZnO nanorods were synthesized by induced seeds by chemical bath deposition using hexamethylenetetramine (HMT) as a precipitant agent and zinc nitrate (ZN) as Zn2+ source at 90°C. The influence of reactants ratio was studied from 2 to 0.25 ZN/HMT molar. The results obtained by scanning electron microscopy confirm that the diameter of nanorods was affected directly by the concentration of both zinc and OH sources. Nanotubes (hollow nanorods) were obtained with high HMT concentrations and were turning over nanorods as HMT concentration decreased. Microstructural information was obtained by Rietveld refinement of grazing incidence X-ray diffraction data. These results evidence low-textured materials with oriented volumes less than 18% coming from (101) planes in Bragg condition.

1. Introduction

Nowadays, the interest in nanostructured ZnO materials has taken more relevance due to its wide range of applications and the scientific interest in polymorphism depending on synthesis conditions. Zinc oxide is a II–VI semiconductor with a band gap of 3.37 eV; it is thermally and chemically stable [1] and presents interesting properties [24]. These properties make the ZnO feasible for applications in many field, such as energy conversion [57], optoelectronics [810] and sensing devices [1114], in particular when it is synthesized in one-dimensional (1D) geometry [1517]. Among all the geometries, the most feasible for these types of applications are nanowires [1, 1820], nanobelts [21, 22], nanotubes and nanorods, and singles or arrays of them [23, 24]. Several methods for the synthesis of nanostructured ZnO have been explored, but some of them are highly power demanding (in temperature or pressure) [25], or they use sophisticated processes to obtain the materials by means of a vapor-liquid-solid mechanisms [2628], that makes the scaling-up a complicated challenge [29]. One of the most promising methods to synthesize nanomaterials is the chemical bath deposition (CBD), which is a non sophisticated, low-temperature (<100°C), and low-cost wet route [2, 25, 30, 31]. Additionally, CBD has a high degree of versatility to modify several parameters, such as temperature, pH [32], and concentration of reactants; which in turn could modify the morphology, size, and shape of the nanomaterials [33].

In this work, we have synthesized ZnO nanorods by CBD and studied the influence of hexamethylenetetramine (HMT) and zinc concentration in their morphology and microstructure. Additionally, the microstructure analysis was realized with Rietveld refinement, using asymmetric diffraction with the grazing incidence X-ray diffraction (GIXRD) technique. Hence, we discuss the low-volume-oriented fraction associated to the preferred orientation obtained, and also we compare sizes obtained by refinement versus scanning electron microscopy (SEM) images.

2. Experimental Details

2.1. Seed Synthesis by Sol-Gel

A solution of 0.01 mol/L of NaOH (SIGMA, 98+%) in methanol was dropped into a 50 mL of 0.005 mol/L dilution of zinc acetate dehydrated in ethanol (Aldrich Chemical Company Inc., 98+%) contained in a three-necked flask with condenser heated at 60°C with stirring. The reaction was performed until the solution became cloudy due to the suspended ZnO particles. The substrates were previously washed and sonicated in methanol two times in periods of 30 min. Afterward, the borosilicate (15×5 mm) substrates were dipped into the colloidal ZnO solution, and then they were dried inclined at room temperature. Finally, they were calcined at 500°C inside an ambient-controlled furnace Neytech for 30 min at around 16 Torr of pressure.

2.2. ZnO Nanorods Growth via CBD

Two experiments with a pair effect of hexamethylenetetramine and zinc nitrate (ZN) were carried out. First experiment consisted in eight samples with constant concentration of HMT and variable ZN content. In the second experiment, six samples with the ZN amount constant while the HMT concentration was varied. The conditions of seed synthesis and impregnation over the substrate were the same for all cases. Table 1 presents the concentrations of reactants utilized in the synthesis.

The growth of ZnO nanorods was realized using a modified method of that reported by Liu and Zhou [34]. The seed-coated substrates were introduced into a 15 mL culture tubes (with screw caps) previously added with constant volume of PEG (0.6 mL). The initial reactants were HMT 0.5 mol/L (Sigma-Aldrich, 99+%), Zn(NO3)2· XH2O (Alfa-Aesar, 99%) 0.25 mol/L and polyethylene glycol (PEG) (J. T. Baker) with PM = 20,000 at around 10 wt%. We mixed adequate volumes of these solutions and tridistilled water in the tubes in order to obtain a total volume of 10 mL, with the final concentrations presented in Table 1. Finally, the tubes were closed to avoid contamination, and they were placed in a temperature-controlled water bath. The reaction was carried out for 3 h at 90°C. After that, the reactors were cooled to room temperature. At the end, the pH in each reactor was registered, and the substrates were rinsed with tridistilled water, then they were calcined at 360°C inside the same ambient-controlled furnace for 30 min at around 16 Torr of pressure.

2.3. Characterization

The morphology of ZnO nanorods was studied using a field emission scanning electron microscope JEOL-JSM 7401-F operated at 3 keV. The micrographs were used to measure length (𝐿) and diameter (𝐷) to obtain 𝐿/𝐷 ratio statistics (56 to 100 individuals for each sample). On the other hand, in order to improve the imaging contrast, a piece of Si wafer was dipped with ZnO seeds following the sequence described above. The morphology of these seeds was studied by SEM.

Diffraction analysis for phase identification and structural refinement were carried out, in GIXRD configuration, using a XPert-Pro panalytical diffractometer operated at 40 kV and 35 mA, equipped with Cu Kα source at 1.54187 Å and PW3011/20 detector. The diffractometer was configured in 𝜔-2𝜃 mode, with incidence angle (𝜔) settled at 1°. The 2𝜃 range was between 25 and 95 degrees with 0.02°-step size and 12 s of step time. Phase identification was realized matching diffracted peaks with PDF cards.

2.4. The Rietveld Refinement Method on GIXRD Configuration

Due to the extensive use of Rietveld refinement programs in diffraction analysis, we used this useful tool for obtaining crystallites size and texture at GIXRD conditions (commonly used for thin films and coatings). The refinement was done with the FullProf (FP) free available software [35], with a modified version of Thompson-Cox-Hastings pseudo-Voigt (TCHZ) function profile. The instrumental resolution function for broadening effects was obtained using a silicon standard from NIST and fitted with the WinPlotr software [36]. Any treatment of smoothing or filtering was carried out on the experimental data. However, due to the asymmetrical condition of GIXRD, that gives higher intensity than those obtained in Bragg-Brentano (BB) configuration, the experimental intensities were corrected to the symmetrical Bragg reflection using the James factor [3739]. This factor relates the asymmetrical and symmetrical diffraction intensities according to𝐽𝐼(2𝜃)=asym(2𝜃)𝐼sym=2(2𝜃)[]1+sen(𝜔)/sen(2𝜃𝜔),(1) where 𝜔 is the incidence angle. In relation to this, Toraya and Okuda [37] multiplied the conventional intensity formula of powder diffraction in their PFLS Rietveld program by 𝐽(2𝜃) in order to employ directly GIXRD data. In our approach, the experimental intensity 𝐼asym(2𝜃) was divided by 𝐽(2𝜃); these corrected values were used in the refinement. Afterwards, we can assume that preferred orientation (PO) subroutine of FP software, available only for BB configuration, could be used with the corrected intensity of experimental diffraction data.

We have considered that size broadening has only the Lorentzian component (𝑌+𝐹(𝑆𝑧)/cos(𝜃)) [40], and microstrains were neglected. The PO function used in Rietveld analysis was the March-Dollase type, commonly used for low-textured materials [41] 𝐺𝑃(𝜙)=21cos2𝜙+sin2𝜙𝐺13/2,(2) where 𝐺1 is a refinable coefficient and represents the degree of texture; 𝜙 is the acute angle between the scattering vector g and the normal to (hkl) plane. According to (2), PO is achieves only if 𝑃(𝜙)>1, and this condition can be present if 𝐺1<1 (in platelet-like habit) or 𝐺1>1 (needle-like habit); 𝐺1=1 means no texture present. In this case, four PO models 𝑃002, 𝑃101, 𝑃110, and 𝑃100 were chosen for each sample in order to fit the PO function, and only one was taken as representative of the sample. The oriented volume fraction was calculated normalizing the (2) and integrating [42]𝑉Oriented=𝜙10(𝑃(𝜙)1)sin𝜙d𝜙(for𝐺1<1),(3) where 𝜙1 is the value when 𝑃(𝜙1) =1. If 𝐺1>1, integration limits change from 𝜙1 to 𝜋/2.

Another diffraction pattern of previously synthesized ZnO was taken as reference of a randomized material due to the fact that its relative intensity matchs with the PDF card no. 36-1451. This material was used to approximate a pole density (PD) of each sample according to Harris method [43]𝑅𝑔𝑖=𝜓𝑖1/𝑁𝑁𝑖𝜓𝑖,(4) where 𝜓𝑖=𝐼(𝑔𝑖)/𝐼𝑟(𝑔𝑖), 𝐼(𝑔𝑖) is the diffracted intensity of (hkl) plane and 𝐼𝑟(𝑔𝑖) is the intensity of each diffracted peak of the sample. The PD data file was used by FP input code control (Algorithm 1) for internal intensity calculation.

! Current global Chi2 (Bragg contrib.) = 1.356
! Files => DAT-file: t2, PCR-file: t2
!Job Npr Nph Nba Nex Nsc Nor Dum Iwg Ilo Ias Res Ste Nre Cry Uni Cor Opt Aut
0      7      1      0      1      0      1      0      0      0      1      4      0      0      0     0      0      0      1
! Resolution file for Pattern# 1
!Ipr Ppl Ioc Mat Pcr Ls1 Ls2 Ls3 NLI Prf Ins Rpa Sym Hkl Fou Sho Ana
  0      0      1      0      1     0      4      0      0      3    10  0      1      1    0      0      1
! lambda1 Lambda2 Ratio Bkpos Wdt Cthm muR AsyLim Rpolarz ->Patt# 1
  1.540560   1.544390    0.4729    20.000    5.5000    0.7998    0.0000       95.00      0.0000
!NCY    Eps    R_at    R_an    R_pr    R_gl  Thmin  Step  Thmax  PSD  Sent0
 50    0.25    0.95  0.95    0.95   0.95      25.1300       0.020006    94.9900    0.000     0.000
! Excluded regions (LowT HighT) for Pattern#  1
 75.00  95.00
  15 !Number of refined parameters
! Zero Code SyCos Code SySin Code  Lambda Code  MORE ->Patt# 1
   0.18066  61.0   −0.10181      0.0   −0.00081      0.0  0.000000    0.00      0
!    Background coefficients/codes for Pattern# 1
 723.16  −855.28       453.03           −79.863        0.0000            0.0000
        21.000 31.000 41.000           51.000    0.000  0.000
!- - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - -   
! Data for PHASE number: 1 ==> Current R_Bragg for Pattern#  1:     3.02
!- - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - - -   
Zincite ZnO
!Nat Dis Ang Pr1 Pr2 Pr3 Jbt Irf Isy Str Furth  ATZ Nvk Npr More
2 00  1.0  0.0  1.002000         162.760    0    7  1
!Jvi Jdi Hel Sol Mom Ter Brind RMua RMub RMuc Jtyp Nsp_Ref Ph_Shift N_Domains
5000001.0000   0.0000.0000  0.00000000
P 63 m c     <- -Space group symbol
!Atom Typ  X      Y      Z Biso     Occ In Fin N_t Spc /Codes
Zn1    Zn          0.33333  0.66667  0.00000  0.00000     2.00000     0    0      0      0
       0.00     0.00 0.00 0.00 0.00
O1 O      0.33333  0.66667  0.37358  0.00000    2.00000      0    0       0     0
   0.00          0.00      121.00    0.00       0.00
!- - - -> Profile Parameters for Pattern #  1
! Scale       Shape1   Bov  Str1  Str2  Str3  Strain-Model
0.84699E-04 0.00000    1.55472     0.00000    0.00000 0.00000    0
 11.00000 0.000 151.000 0.000 0.000 0.000
!     U    V      W       X    Y GauSiz LorSiz Size-Model
 0.000000   0.0000000.0000000.0000000.0161110.0000000.560394−1
  0.000 0.000 0.000 0.000 141.000 0.000 131.000
!       a  b          c         alpha beta    gamma #Cell Info
 3.251389 3.251389 5.209196 90.000000 90.000000 120.000000
 71.00000 71.00000 81.00000      0.00000       0.00000    71.00000
!     Pref1   Pref2              Asy1      Asy2            Asy3            Asy4   S_L      D_L
 0.92047 0.00000 −0.11362 −0.02108 0.00000 0.00000 0.05815 0.01090
     91.00    0.00 101.00    111.00        0.00      0.00        0.00 0.00
       0.0000      0.0000    2.0000      Platelet-Needle vector (Size)
! 2Th1/TOF1 2Th2/TOF2 Pattern # 1
   25.130     75.000   1

3. Results and Discussion

3.1. Seed Analysis

Figure 1(a) shows SEM micrograph of ZnO seeds deposited over a glass substrate and calcined at 500°C. Most of seeds dimensions are in 15–30 nm (diameter), and some of them reach the 50 nm. The uniformity of particles is evident in the majority of substrate surface; however, unavoidable local inhomogeneities are present in the synthesis as a consequence of nonuniform evaporation step.

On the other hand, the thermal treatment at 500°C in low-vacuum atmosphere has mainly three effects: (i) first of all, it generated more dense particles as a consequence of liquid evaporation and elimination of residues from the sol-gel reaction, (ii) secondly, it increased the size of particles from colloidal agglomerates until final sizes (<30 nm), and (iii) finally, it ensured strong adherence of seeds on the glass substrate. The seeds act as a nucleation center with low-activation energy barrier for anisotropic growth of ZnO nanorods along [001] direction [6, 16, 44].

Figure 1(b) shows semialigned nanorods grown from ZnO nuclei; the electrostatic attraction of ionic species (Zn2+ and OH) in polar surfaces causes nucleation [25] and consequently an anisotropic growth.

3.2. Morphology and Growth of ZnO Nanorods

Figure 2 (Z1–Z8) shows secondary electron SEM micrographs of the nanorods as a function of ZN concentration. It can be observed systematic changes in the shape of the nanorods, due to the variation of precursor concentration. It demonstrates the importance of the ZN concentration to obtain a particular shape of nanorods. First 3 images (Z1–Z3) show slightly porous nanorods, and the diameters are not uniform. In the case of Z2, most of the nanorods are broken approximately at the middle section. It is probably due to a thermal effect, as a result of the porosity and less uniformity generated in the nanorods at these concentration ratio. According to Chen and Gao [45], the reaction can be expressed as follows:CH26N4+6H2O6HCHO+4NH3,(5)NH3+H2ONH+4+OH,(6)2OH+Zn2+ZnO(s)+H2O.(7) From these equations, it can be shown how HMT two-step hydrolysis generates OHspecies that potentially react with Zn2+ cations which are coming from the ZN. One molecule of HMT reacts with two Zn2+ cations and produces two molecules of ZnO. This stoichiometric ratio corresponds to Z01 sample. Hence, the Z02 to Z08 samples are under stoichiometric ratio (HMT excess). Secondary electron SEM micrographs of samples Z01 to Z08 show basically a decreases of the diameter of rods as the ZN concentration decrease. This could be explained as the competition of the Zn2+ ions; near the stoichiometric region, there is no excess of species, and competition takes place in a ZnO seed face that induces growing by OH-. According to our synthesis condition, we consider a constant number of seeds particles available on the substrate (constant area). Then, if ZN concentration decreases over a constant available seed induction faces, thin nanorods growing in [001] direction are expected. Figure 3 shows average diameter of nanorods (obtained by direct account of nanorods population) and final pH of samples versus ZN concentration. It is evident that the diameter of nanorods diminished systematically as the growing agent (ZN) decreased. This is in agreement with data obtained from reaction time variation reported elsewhere [46, 47], and also it is consistent with material conservation law. According to the graph, final pH increased from almost neutral (6.9) in Z1 to alkaline (8.4) in Z8. This fact coincides with (5) to (7); when the concentration of cation Zn2+ is low, the amount of non reacted hydroxyl (OH) formed from HMT hydrolysis increases, and then the pH increases as well.

Figure 4 shows SEM micrographs of nanorods synthesized in the second experiment. Although the ZN/HMT ratios were similar in some samples (e.g., Z07 and Z10 have both 0.5 of ZN/HMT ratio), the concentrations of reactants vary, and therefore, these samples also presented structural and morphological differences.

In Figure 4, SEM micrographs of samples Z10 to Z14 with a hollow rod structure (nanotube-like) are shown, and their wall thicknesses were ca. 30 nm, present neither in Z9 nor in the previous experiment (samples Z1 to Z8).

Nanotube-like structure appears in Z10 with thin wall tip; however, most of them are destroyed or not well defined. We have commented the presence of ZN, as a source of Zn2+, necessary for the growing of nanorods. In these experiments, as the HMT content increased, the reaction required more water (via HMT hydrolysis), then water concentration constituted a limiting factor in the chemical reaction. In the constant volume reaction (10 mL), the total water (added and used for dilution) was not enough for the hydrolysis (5) and (6), and the chemical reaction was limited in samples Z12 to Z14.

Accordingly, Z12 to Z14 presented similar nanotube-like morphologies, as it can be seen in SEM micrographs (Figure 4). In Figure 5, it is shown that nanorods diameter increased as HMT concentration increased (samples Z9 to Z11); due to limited reaction progress, samples Z12 to Z14 were excluded. Indeed, it can be observed that influence of HMT concentration in diameter of nanorods was lower than the influence of ZN in previous experiment (Z1 to Z8). Final pH values presented low variation and were around 7.0.

A hypothesis of hollow formation mechanism is based on amphoteric properties of ZnO when it redissolves to form zincates (ZnO2−2) or hydroxo complexes as Me+[Zn(OH)3]- in basic media [33, 48]. In a medium with Zn2+ cations and OH species coming from HMT hydrolysis, nanorod growth starts; however, a continuous supply of OH prevails during the reaction. Then, in the basic media, ZnO complexes could be formed and redissolution phenomena of nanorods in polar face (002) could take place. Finally, hollow nanorods could be formed. After redissolution, pH was lowered around 7.0, as it was observed experimentally.

3.2.1. Phase Analysis

GIXRD patterns of ZnO nanorod samples are shown in Figure 6. Phase analysis was similar to conventional powder methods [49]. The only phase detected corresponded to crystalline hexagonal wurtzite type structure (PDF card no. 36-1451). All diffractograms show relatives intensities as a typical ZnO powder sample.

The nonuniformity of the material observed in SEM images is also reflected in peaks intensity of diffractograms. The (002) planes reach their minimum intensity in Z04 sample probably due to a poorly coated substrate; in other hand, (002) reflection becomes the most intense in Z07 sample where more amount of material was present.

The effect of hollow nanorods is evident in GIXRD patterns of samples Z9 to Z14. If hollows are present, the amount of (100), (002), and (101) diffracting planes diminishes directly; as a consequence, peak intensity decreases. Intensities in diffractograms of ZnO nanorods in Z1-Z8 samples are higher than those observed in nanotube-like samples Z9–Z14.

Additionally, diffractograms of samples Z11 to Z14 are similar; they show consistency with the limited reaction progress for these samples, as discussed before.

3.2.2. Rietveld Analysis

Figure 7 shows James factor 𝐽(2𝜃) at different incidence angles, as a function of 2𝜃. Only a slight variation (<10%) is observed at low 2𝜃 (<30°) for 𝜔=1. According to the graph, the factor varies considerably at low 2𝜃, when incidence angle increases (𝜔5). A simulated and experimental (corrected) diffractogram are shown in Figure 8. In our case, the correction was approximately to divide by 2 the experimental GIXRD data. No peak broadening was affected by the correction.

The main results of Rietveld refinement are summarized in Table 2; additionally, typical FP input control code is appended at the end of the document. From Table 2, it can be seen a reasonable goodness of fit index (GofF) reached for almost all refinements, indicating an acceptable structure simulation of experimental data. An exemption is Z4 refinement, that presented high residuals possibly due to the low intensities of diffracting peaks, and as a result, the high noise coming from the amorphous substrate. Lattice parameters, 𝑎 (3.250 ± 0.003) and 𝑐 (5.207 ± 0.005) and 𝑐/𝑎 ratio (1.602 ± 0.003) obtained by refinement show typical values of wurtzite type structure of ZnO.

Four models 𝑃hkl of PO were assumed for each sample giving a total of 56 cases; in all the cases, the residuals 𝑅𝑝 and 𝑅wp of the vectors were very low and did not exceed the 0.7 of standard deviation. For this reason, the selection of the PO vector was based on the higher percentage of volume oriented in each sample and not on the less residuals 𝑅𝑝 and 𝑅wp. The total results of 56 refinements were not shown in Table 2; only were presented these results that belong to the selected PO models. In all cases, the 𝑃101 model normal to (101) plane was selected. The volume of oriented crystals (see Table 2) associated to these models vary from 4.7 to 18% with a mean volume of 11.3%, indicating that this CBD synthesis results in low-aligned materials (low texture) unlike previously reported works [23, 24, 50]. According to March-Dollase function, the values of 𝐺1 parameter indicate shape diffracting domains: platelet or needle-like. In all cases, the refined parameter 𝐺1 of (101) plane was <1, then platelet-like habits resulted.

Figure 9 shows (101) planes, and it compares shapes of habits in low-index planes. If the area of the section increased, the shape of the habits approaches to platelet-type. The (101) plane habit can be seen as an array of distorted hexagonal platelet. When 𝑃101, 𝑃110, and 𝑃110. PO models were chosen, the platelet habits result (𝐺1<1). On the contrary, the (002) plane has the smaller sectional area in a nanorod; when 𝑃002 model was selected (results not included), 𝐺1 became slightly > 1 (in all cases), which means that needle-like habits were obtained.

The (101) model of PO is discussed here. In Figure 10 is sketched a cross-sectional cut of hexagonal inclined ZnO rod and the diffraction conditions in both BB and GIXRD configuration. During the scanning in GIXRD experiment, the detector finds a reinforced scattering of X-rays at (2𝜃Bragg𝜔) position with a dispersion vector normal to diffracting planes (not to the surface) named 𝑄𝐴𝑆. In contrary to BB geometry, the planes parallel to the surface will not diffract in GIXRD, unless 𝜃Bragg=𝜔. Only one angle of rod inclination, (𝛾), satisfies 𝑄AS condition for any diffracted intensity (𝑖), and this inclination can be expressed as𝛾𝑖=𝜃2𝜃Bragg,𝑖𝜔2,(8) where 𝜃 is the angle between (hkl) plane and the axial [001] vector; 𝜔 is the incidence angle, and 2𝜃Bragg,i is the Bragg angle for the intensity 𝑖. Some values of ZnO nanorod’s inclinations, 𝛾, calculated using (8) are presented in Table 3. The calculated angle in (101) corresponds to the inclination of oriented ZnO population in Bragg condition (quantified in fraction-oriented volume), and it is consistent with SEM images.

Size values related to length (𝐿002 or 𝐿), diameter (𝐿100 or 𝐷), and 𝐿/𝐷 ratio obtained by Rietveld refinement, and also from SEM images, are presented in Table 4.

The nature of evident differences of length and diameter in the techniques is related to the size of the coherent domains rather than the grain size obtained by scanning microscopy [51]. However, two aspects of the 𝐿/𝐷 ratio will be briefly treated next. First, some information can give the shape of diffracting domains. Low values of 𝐿/𝐷 ratios obtained by GIXRD regarding which SEM values could be indicative of anisotropy in diffracting domains, is not as high as in nanorods. Ratios of 1.2 to 3 suggest semielliptical domains, and they agree with platelet-type-calculated habits. And second is the nature of GIXRD technique. A low resolution with a strong peak broadening in GIXRD compared to parafocusing geometry could indicate that the values obtained are in the resolution limit to this optical arrangement. In spite of that, the second experiment (Z9–Z14) ratio tendency is the same as the obtained by SEM.

Overall isotropic temperature factor 𝐵 and 𝑧 position of oxygen atom were also refined. These parameters are intensity dependent unlike these related to peak broadening (e.g., size effects) or peak position (e.g., lattice parameters). The GIXRD experimental data has been corrected as described before divided by a factor near to 2 in all the scanning range. Although the intensity has been divided, the average 𝐵 of 1.74 ± 0.6 Å2 and 𝑧 values lie in range.

4. Conclusions

The growth of ZnO nanorods was realized by CBD seed-assisted synthesis. The concentrations of both ZN and HMT reactants influenced directly on the diameter of nanorod; this was determined by the availability of zinc source for the growing of nanorods over constant nucleation centers and the concentration of precipitant agent. However, hollowed-type structures were formed when OH excess by HMT hydrolysis was present.

Rietveld analysis of GIXRD-corrected data has been performed. Correction of asymmetrical to symmetrical diffraction condition is a formalism that lets us combine the use of refinement software FullProf with a surface-sensitive X-ray characterization technique. The information obtained by refinement from reflection position and peak shape did not change with correction as intensity-dependant parameters (𝐵ov,𝑧) did. Results show typical 𝑐/𝑎 values of 1.602, a unique PO vector (101) to define the main volume-oriented rod population, and finally crystallite size that suggests elliptical diffracting domains.


The authors appreciate the technical assistance from Enrique Torres, Carlos Ornelas, Silvia Miranda, and Miriam Moreno (CIMAV, Chihuahua).