Research Article | Open Access
V. G. Il’ves, S. Yu. Sokovnin, "Structural and Magnetic Properties of Nanopowders and Coatings of Carbon-Doped Zinc Oxide Prepared by Pulsed Electron Beam Evaporation", Journal of Nanotechnology, vol. 2017, Article ID 4628193, 11 pages, 2017. https://doi.org/10.1155/2017/4628193
Structural and Magnetic Properties of Nanopowders and Coatings of Carbon-Doped Zinc Oxide Prepared by Pulsed Electron Beam Evaporation
With the help of electron beam evaporation of mechanical mixtures of nonmagnetic micron powders ZnO and carbon in vacuum with the subsequent annealing of evaporation products in air at the temperature of 773 K, single-phase crystal nanopowders ZnO-C were produced with the hexagonal wurtzite structure and low content of the carbon dopant not exceeding 0.25 wt%. It was established that doping ZnO with carbon stimulates primary growth of nanoparticles along the direction in the coatings. Nanocrystal growth in coatings occurs in the same way as crystal growth in thin films, with growth anisotropy in the -axis direction in wurtzite ZnO. Element mapping has confirmed homogeneous distribution of carbon in ZnO lattice. Ferromagnetism of single-phase crystal nanopowders ZnO-C with the hexagonal wurtzite structure and low content of the carbon dopant not exceeding 0.25 wt% was produced at room temperature. Ferromagnetic response of the doped NP ZnO-C has exceeded the ferromagnetic response of pure NP ZnO 5 times. The anhysteretic form of magnetization curves NP ZnO-C indicates aspiration of samples to superparamagnetism manifestation.
The diluted magnetic semiconductors (DMS) cause huge interest due to their potential use in devices of spintronics [1, 2]. In particular, magnetism of nondoped ZnO is the object of scientific debates because d-orbitals of Zn in nonmagnetic stoichiometric ZnO are completely filled . Occurrence of ferromagnetism at the room temperature (RTFM) in ZnO is connected to the presence of oxygen vacancies () [4, 5], vacancies of Zn () [6, 7], and interstitial atoms Zn () . It is theoretically shown [9, 10] that has the magnetic moment. Xing et al.  reported RTFM in ZnO nanowires and attributed it to the presence of oxygen vacancies. Detailed theoretical research of the vacancy-induced magnetism in ZnO thin films has shown [12, 13] that RTFM of films occurs due to , but not due to .
Various methods were used for synthesis of nanoparticles and films of ZnO-C. In calculations, Pan et al.  have predicted RTFM in C-doped wurtzite ZnO and then, by means of pulsed laser deposition (PLD), produced ZnO-C films with the Curie temperature over 403 K. Zhou et al.  received ZnO-C films with RTFM by means of ionic implantation. From this point on, publications about detection of RTFM in carbon-doped ZnO began to appear even more frequently [15–20]. Enhancement of room temperature ferromagnetism in C-doped ZnO films by nitrogen codoping was described in .
The coexistence of two ferromagnetic phases ZnO in the carbon-doped nanoparticles of ZnO produced by the zol-gel method with two points of the Curie (>773 K) and metamagnetic transformation in the magnetic field of = 19.2 kOe is shown in the study . However, the main issue is the origin of the magnetic moment in the ZnO-C system because it has no magnetic dopants of transitional elements. Therefore, it is impossible to neglect the role of internal defects in pure ZnO, for which strong correlation between defects and magnetization is proved in numerous works . Occurrence of RTFM in various nanomaterials is influenced by a large number of factors; in particular, the way of nanomaterials receipt strongly influences their magnetic properties .
Electron beam is a powerful tool for the creation of defects in a solid state. Nevertheless, there are few researches of RTFM in DMS, such as in ZnO-based nanomaterials, which were carried out with the use of an electron beam [25–29]. At the same time, electron beam of electronic microscopes  is frequently used for the modification of semiconductors or for receiving high-quality thin films [31, 32] on electronic installations based on channel spark-type discharge.
Relativistic electron beam is successfully used for receiving nanoparticles of various compounds in industrial-and-trial volume in the installation on the basis of the industrial accelerator with electron energy of 1,4 MeV and electron beam extraction into the air [33, 34]. The installation is expensive even though it has high capacity. Besides, upon evaporation in the atmosphere under normal pressure, formation of the large spherical and poorly agglomerated nanoparticles occurs. Those nanoparticles have a smaller density of various defects in contrast to the density of defects in the nanoparticles formed when produced in the vacuum.
Nevertheless, RTFM was observed in thin films of ZnO-C prepared by electron beam evaporation . Data of the last researches of the ZnO-C [35, 36] system show that it is insufficiently studied and has large prospects. Thus, aside from the magnetism, the ZnO-C system is quite promising because of its luminescent, optical properties [22, 37] and the increased photocatalytic activity [38, 39].
The purpose of this study was synthesis and research of structural properties of ZnO doped by carbon in small concentration by the method of target evaporation with the use of the pulsed electron beam in the vacuum and low-pressure gas .
Nanopowders (NPs) of pure and carbon-doped ZnO were deposited on glass and titanic substrates on the nanobeam-2 installation . During the deposition, temperature of substrates was approximately at 373–473 K. Residual air pressure in the vaporizing chamber did not exceed 4 Pa. The distance between the target and the substrates was about 10–15 cm. Mode of evaporation was as follows: an accelerating voltage: 40 kV, electron beam current: 0,4 A, pulse length: 100 μs, pulse repetition rate: 100 Hz, beam scanning on target: 2,5 sm2, and time of evaporation: 40–50 min.
Targets were prepared by mechanical stirring in a porcelain mortar of ZnO micron powders of pure for analysis (GOST 10262-73) with the specific surface area = 2,7 m2 and spectral pure graphite (99.999). Concentration of added carbon was amounted to 0.1 and 0.5% wt. Mass of the targets with the diameter of 40 mm and height of 15–20 mm amounted to about 60–70 g.
All the NPs were deposited at room temperature and subsequently annealed at 773 K in air for 1 h. The following diagnostics of nanopowders were used in the experiments. The percentages of Fe () impurities in the samples were checked by an ELAN 9000 Perkin Elmer SCIEX (inductively coupled plasma (ICP)). Method of atomic absorption spectrophotometry (AAS) on Perkin-Elmer spectrometer was used for determination of carbon concentration.
The crystal structures of the ZnO (ZnO-Zn) and NPs and bulk samples were characterized by Shimadzu X-ray diffractometer XRD-7000 with nickel-filtered Cu Kα radiation ( = 0.154 nm) in a 2θ range 20°–90°. SEM images, EDX analysis, and elemental mapping were measured by scanning electron microscopes LEO982 with Oxford X-Ray Detector and LYRA3 TESCAN. The surface morphologies and sizes of the sample ZnO (ZnO-Zn) were observed by a JEOL (Japan) JEM 2100 Transmission Electron Microscope (TEM) using an accelerating voltage of 200 kV. TEM was performed after the particles sedimented on carbon-coated copper grids. Specific surface area () of NPs was defined by the Brunauer-Emmett-Teller method on the Micromeritics TriStar 3000 installation. Fast Fourier transform (FFT) was performed on lattice images with ImageJ software to obtain diffraction patterns. The magnetic measurements were performed on Cryogenic CFS-9T-CVTI vibrating sample magnetometer (VSM).
3. Results and Discussions
According to X-ray diffraction (XRD) upon evaporation of targets from pure ZnO, two-phase amorphous-nanocrystalline powders ZnO-Zn with = 36 m2/g and high content of metal nanoparticles of zinc (~40 wt.%) were produced. Further on, ZnO-Zn NPs were annealed in the alundum crucibles on air at the temperature of 773 K within 1 hour in the chamber electric furnace.
Doped ZnO-C NPs were produced by evaporation of carbon-doped targets achieved by multiphase ZnO-Zn-C NPs and were also annealed at the temperature of 773 K within 1 hour. Annealing of NP, previously collected from glass substrates, was performed in the alundum crucibles. ZnO-Zn-C NPs, deposited on titanic substrates, were annealed together with substrates.
Prior to that, ZnO-Zn (ZnO-Zn-C) NP had black color. After annealing, powders gained white color with a weak shade of gray.
Choice of annealing temperature was justified by the fact that annealing at the temperature over 773 K is very critical for magnetism in the ZnO-based systems .
Results of measurements of and element composition of powders are presented in Table 1. It is obvious that concentration of iron impurity in a high doped sample of ZnO-C (sample number 4, Table 1) is rather low, below 100 ppm.
| sample number 2 is produced by evaporation of the target from ZnO with the air pressure of 20 Pa.|
concentration of from three sites of each sample is given.
, this numbering of NPs samples is used.
X-ray diffraction patterns of annealed NPs of pure and carbon-doped ZnO ( = 0; 0.24 and 0.25 wt%) are shown in Figure 1.
All peaks on diffraction patterns correspond to hexagonal wurtzite structure of ZnO with the space group P63mc (Joint Committee on Powder Diffraction Standards (JCPDS) the card number 36-1451). Additional peaks from pure carbon or carbon-containing phases are absent on the diffraction patterns.
Relative comparison of ratios of the integral intensities 002/100, 002/101 of three main XRD peaks (100), (002) and (101) (Table 2) show that the sample of C-doped ZnO No. 3 had the smallest peak intensity (002).
| intensity is specified.|
At the beginning, relative peak intensity (002) decreases upon doping with carbon concentration growth (). Further on, the relative intensity of the peak 002 increases again.
Crystal size was estimated using the Scherrer formula . Results of the calculation presented in Table 2. It proves that carbon doping of pure ZnO stimulates primary growth of NPles along the direction in coatings from ZnO NPles formed upon NPles deposition on the cold glass substrates; that is, nanocrystals growth in coatings occurs similar to crystals growth in thin films, with growth anisotropy in the direction of the -axis in wurtzite ZnO.
Relative growth of the peak 002 is indicative of the strengthening of crystals growth upon annealing in the direction of the axis with carbon concentration increase. It is obvious from the Table 2 that the average size of crystallites in sample number 4 (50 nm) is significantly higher than in the slightly doped sample number 3 (33 nm). The ionic radius of C4− (0.260 nm) is much larger than that of O2− (0.140 nm) ; the substitution of O by C will expand the lattice. The expansion of the ZnO lattice might also originate from C atoms located at interstitial sites or from defects induced by pulsed electron beam evaporation.
We will note that parameters of hexagonal lattice and their relation to / for NPs of pure and doped ZnO (Table 2) considerably prevail over similar parameters of the microcrystalline standard. The slight variation of and may be due to partial substitution of lattice oxygen by carbon as well as the presence of interstitial carbon atoms in the ZnO lattice.
Determination of carbon concentration in the ZnO-C system is not a trivial task. Carbon, stable at the room temperature, upon ambient temperature increase above 673 K, begins to interact actively with residual oxygen atoms with carbon dioxide formation, which creates problems upon concentration assessment in the carbon-doped nanostructures . Carbon concentration in NP samples was determined by the methods of atomic absorption spectrophotometry (AAS) and the energy dispersive X-ray (EDX). We will note that carbon concentration in ZnO-C NP determined by the atomic absorption spectrophotometry methods (AAS) was slightly lower than in the targets (0.24 and 0.25 wt.% for targets ZnO-0.1 wt% and ZnO-0.5 wt% C, resp (Table 1)). On the contrary, C concentration in the samples determined by the EDX method was 10 times higher than the concentration estimates by the AAS method.
The following unwanted factors could also affect the observed mismatch in the concentration of carbon defined by the AAS and EDX methods: not enough fine vacuum in the scanning electron microscope (the microscope LEO982 had very old vacuum system) or hit of oil vapors into the researched samples in the course of their synthesis in installation NANOBIM-2, where oil-diffusion pumps for pumping of the evaporation camera are used. Similar divergence of carbon concentration in targets and C-doped ZnO thin films prepared by electron beam evaporation (“the nominally 1 at.% C sample was found to contain 0.25% C while the nominally 3% sample contained 1.9% carbon”) was observed in the process .
It is known  that determination of carbon concentration by AAS method is more preferable in comparison with the EDX method; therefore, further on we used the values of C concentration in the samples received by this method.
Evaporation in vacuum by means of the pulsed electron beam [43, 44] usually leads to high-temperature decomposition of ZnO with formation of a significant amount till 30–40 wt% [45–47] of metal NPles of Zn, less than 5 nm in size (Figures 2(a) and 2(b)).
At the same time, oxide NPles in two-phase ZnO-Zn NP have a bit larger size, up to 15 nm, than the restored metal NPles of Zn. In fact, bimodal distribution of metal and oxide NPles by size is observed.
Quasi-spherical crystalline metal-oxide NPles of ZnO-Zn, in their turn, form agglomerates of NPles upon their receipt which is well visible on HRTEM picture (Figure 2(b)).
Figure 2(b) shows the interlayer spacing is about 0.285 nm which corresponds to the interlayer distance of the (100) crystal plane of wurtzite ZnO.
We will note that the existence of the amorphous phase in ZnO-Zn NPs was formed during NPles hardening upon their deposition on a cold substrate (usual windowpane glass). Figure 2(d) shows the fast FFT to amorphous region unannealed sample ZnO-Zn. Insets of Figure 2(c) are the corresponding FFT images from crystalline region.
Typical spherical core-shell ZnO-Zn nanoparticle is shown in Figure 2(e). Thickness of the shell can reach nanometer units (3–5 nm) and both unevenly and not completely cover the crystal core.
SEM image of ZnO-Zn NP previously deposited on titanic foil in vacuum and then annealed in air at the temperature of 500°C within 1 hour is presented in Figure 2(f). It is interesting that the agglomerated quasi-spherical NPles of ZnO-Zn (Figures 2(a) and 2(b)), after annealing in air at 773 K, were transformed into relatively poorly agglomerated quasi-spherical NPles (Figure 2) with sizes close to each other.
In the SEM image (Figure 2(f)) shown agglomerates consist of the spherical, almost monodisperse, NPles created after annealing. The size of the annealed spherical ZnO NPles does not exceed 50 nm which is consistent with the dependence of ZnO NPles size change during annealing on air as described in the study .
It can be considered as determined that in the result of NP ZnO-Zn annealing at 773 K the initial quasi-spherical metal-oxide NPles with bimodal distribution by the size were transformed to quasi-spherical NPles of ZnO less than 50 nm in size. Such transformation of the NPles formed during annealing indicates the strong recrystallization growth of metal particles of Zn after their oxidation, in the result of which sizes of the initial and newly formed NPles of ZnO align among each other.
It should be noted that, according to TG-DSC analysis, in the process of ZnO-Zn NP heating, oxidation of Zn metal particles in two-phase mixture begins at a very low temperature, about 430 K . Moreover, in small concentrations (0.24 wt.%) carbon-doped ZnO initially caused the size of grains to decrease from 40 to 30 nm, which is confirmed by the high of the ZnO-C sample ( = 11.16 m2/g, sample number 3, Table 1). Reduction of the grain size is possibly related to the replacement of oxygen atoms in ZnO lattice sites with small atoms of carbon.
According to XRD analysis, with the further growth of carbon concentration, the grain size increased up to 50 nm again. Growth of grain can be explained by simultaneous coexistence of two solution types in the lattice of ZnO-substitutional solid solution and interstitial solid solution and also by the emergence of some quantity of free carbon which did not enter the ZnO lattice. The replacement of Zn ions with carbon ions () and introduction of carbon in interstitials was observed in the study [12, 50].
Figure 3 shows the morphology of coatings from the NPles of pure and C-doped ZnO deposited on a titanic foil and then annealed together with the foil on air at the temperature of 773 K within 1 hour. All coatings generally consist of NPles and spherical globules (droplets) of the micron size formed by these NPles. Bimodal distribution of particles by the size, typical for electron beam evaporation, is well visible [45, 51, 52]. We will also note the existence of an insignificant number of nanorods pointed at by the arrows in Figure 3(b). The biggest globules in the coating from pure ZnO have the size less than 1 μm; the size of the majority of globules does not exceed 0.5 μm.
(a) Number 1
(b) Number 1
(c) Number 3
(d) Number 3
(e) Number 4
(f) Number 4
(g) Number 3
(h) Number 4
Upon carbon addition, the quantity of globules increases. The maximum size of globules reaches 3 μm (Figure 3(c)); however, the structure of the coating will change significantly. Break down of globules of the average size (0.5 μm) to the size less than 0.1 μm occurs (Figure 3(d)). The surface of a globule resembles the form of a “sea hedgehog” (Figure 3(g)). Judging by the numerous prints of the round and oval shape on a coating surface (shown by arrows in Figure 3(c)) remaining from the globules that have fallen off the coating, globules adhesion force with the surface is insignificant.
With the further increase of carbon concentration in a coating, noticeable growth of a number of large globules up to 3 μm in size occurs. In Figure 3(e), the tendency towards size increase, surface smoothing (Figure 3(f)), formation of globules of perfect spherical shape (Figure 3(h)), and, respectively, reduction of globules of the average size is well observed.
The change of coatings morphology on the basis of ZnO during doping as a result of the size change of the average-sized globules correlates well with the parameters of their (Table 2) and change of grain size from XRD data.
It should be pointed out that the spherical shape of globules, perfect, close to ideal, in sample number 4 (Figures 3(e), 3(f), and 3(h)) indicates strong agglomeration of grains between each other which contributes to FM strengthening of ZnO particles, in accordance with the study conclusions [53, 54].
Upon doping, it is very important to receive homogeneous distribution of the dopant by volume or surface of the sample. For the research of uniformity of carbon distribution in the ZnO lattice, element mapping of samples was implemented. Data of samples mapping with different concentrations of carbon are presented in Table 3.
Lack of clusters and homogeneous distribution of carbon in the samples is well visible. Comparison of color saturation on Table 3(e and k) directly points to a big concentration of carbon in sample number 4 in contrast to sample number 3.
RTFM was found in all samples of pure and carbon-doped ZnO produced with the use of pulsed electron beam evaporation.
S-shaped hysteresis loops Figure 4(a) were found in NPs samples of nondoped ZnO at the room temperature.
It is visible from Figure 4(a) that magnetization of the sample produced in vacuum exceeds magnetization of the sample evaporated in the air even after annealing almost twice. The identical form and symbate behavior of hysteresis loops of both samples indirectly prove that ferromagnetism (FM) of the samples is caused by the same type of defects.
Higher magnetization value of the sample evaporated in vacuum denotes higher concentration of structural vacancies ( and/or ) in sample number 1 as compared with sample number 2 (Table 1), which is natural, since nanoparticles formation took place upon oxygen deficiency. The S-shaped form of the hysteresis loop indicates superposition of ferro- and diamagnetic responses in the samples.
Considering a significant error of magnetization measurement used in VSM magnetometer operation ( = ±0.001 emu), comparison of absolute values of indicators of specific magnetization (emu/g), which are often comparable with the measuring background in terms of size, seems to be not quite correct. However, a qualitative assessment of the behavior of the magnetic moment is entirely permissible.
In the ZnO-C system, suppression of diamagnetic components is expressed stronger than in ZnO samples No. 1 and 2. Nevertheless, S-shaped form of magnetization curves indicates superposition of two deposits, ferro- and diamagnetic, which indicates significant influence of ZnO lattice.
The anhysteretic form of magnetization curves of both samples (No. 3 and 4) indicates samples pursuance of superparamagnetism. Previously, superparamagnetism was observed in nondoped ZnO  as well, and it was explained by the cooperative streamlining of the superparamagnetic nanograins forming a cluster. Superparamagnetism was also found in the nondoped ZnO nanorods . The anhysteretic magnetization curves of C-doped ZnO thin films were obtained in the study .
Chemical analysis of sample number 4 with the maximum carbon concentration showed (Table 1) that content of Fe impurity does not exceed 0.01 wt.% (100 ppm). Ferromagnetic response from such amount of iron impurity is considerably smaller than the observed magnetic response (Figure 4(b)); therefore, the impurity model of the magnetism is not applicable here.
Thus, in both doped ZnO-C samples RTFM was clearly observed as a result of carbon inclusion into the ZnO matrix. The maximum magnetic moment is determined in the sample with the nominal content of of 2.4 wt% C. Earlier in ZnO-C films, the maximum moment at C concentration of 1 at.% [14, 35] and reduction of the magnetic moment at higher C concentrations 49 were observed. Such behavior was interpreted as a tendency of carbon atoms to be distributed nonuniformly at high concentrations.
In the research , the growth of magnetization with the increase of dopant concentration up to 2 at.% was also observed. At C = 2 at.%, the magnetization curve achieved saturation by the maximum of saturation of = 1.1 emu/g. Upon further carbon doping, only insignificant fluctuation of magnetization in films was detected.
The RTFM mechanism in ZnO-C has been earlier suggested by Pan et al. . Strong interaction of s- and p-orbitals of carbon with s-orbital of zinc leads to splitting of 2p-orbitals of carbon near the Fermi energy level, which provides primary contribution to the magnetic moment. Localized 2p of the carbon spins are coupled with the holes in O 2p states generated in the result of oxygen replacement in sites with carbon. Such p-p interaction induces global ferromagnetism in the ZnO-C system.
Pure and carbon-doped NPles of ZnO are synthesized by the method of the pulsed electron beam evaporation. The samples were annealed at the temperature of 773 K. The XRD analysis confirmed the hexagonal wurtzite structure of the samples. With the growth of carbon concentration, the nonmonotonic change of lattice parameters and growth of crystal ZnO-C grains were observed.
NPles sizes calculated according to the data of BET analysis are consistent with the NPles sizes received from XRD analysis.
It is found that ZnO doping by carbon stimulates the primary growth of NPles along the direction in the coatings formed upon NPles deposition on the cold substrates; that is, nanocrystals growth in coatings occurs similar to crystals growth in thin films, with the growth anisotropy in the direction of the -axis in wurtzite ZnO. The SEM analysis has shown transformation of ZnO-Zn NPles after annealing at the temperature of 773 K in monodispersed spherical ZnO NPles with an average size of about 50 nm. With the growth of carbon concentration, the number of droplets on the surface of ZnO deposited on substrates increases.
The change of coatings morphology on the basis of ZnO during doping as a result of globules size change correlates well with the parameters of their and change of the grains size from XRD data. The element mapping confirmed homogeneous distribution of carbon in ZnO when using the method of pulsed electron evaporation of powders’ mechanical mixtures. Magnetization of the annealed ZnO sample produced in vacuum is two times higher than magnetization of the annealed sample produced in the air atmosphere due to the higher density of oxygen vacancies in the sample formed in the oxygen deficiency. FM response of carbon-doped samples was 5 times higher than the magnetic response of nondoped samples. With the growth of carbon concentration, magnetization of samples increased. Anhysteretic curves are indicative of ZnO-C nanoparticles pursuance of superparamagnetism.
This manuscript has been presented as a poster in 13th International Conference Modification of Materials with Particle Beams and Plasma Flows.
Conflicts of Interest
The authors declare that they have no conflicts of interest.
The authors are grateful to the employee of IMET of the Ural Branch of the Russian Academy of Sciences (UB RAS), to Candidate of Chemical Sciences, S. V. Pryanichnikov, for the X-ray phase analysis, to employees of IEP UB RAS: Junior Research Assistant, T. M. Demina, for measurement of a specific surface area and the DSC-TG-analysis, and to Candidate of Physical and Mathematical Sciences, A. M. Murzakaev, and Junior Research Assistant, O. R. Timoshenkova, for TEM and SEM shooting of samples. This study was done within the subject of the State Task no. 0389-2014-0005 and was partially supported by the Russian Foundation for Basic Research Project no. 15-08-01381.
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