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Advances in Condensed Matter Physics
Volume 2014 (2014), Article ID 806327, 6 pages
Defects Induced Room Temperature Ferromagnetism in ZnO Thin Films
School of Materials Science and Engineering, Hebei University of Technology, Tianjin 300130, China
Received 2 December 2013; Accepted 27 December 2013; Published 19 February 2014
Academic Editor: Shoubao Zhang
Copyright © 2014 Xiao Zhang et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.
Polycrystalline ZnO thin films are prepared by the co-sputtering method under different oxygen partial pressures. Films deposited in pure argon gas exhibit ferromagnetism, whereas other films deposited under different oxygen partial pressures are diamagnetism. XPS results show the presence of Zn interstitial and oxygen vacancy in all of samples. Further analysis indicates that Zn interstitial may play an important role in triggering magnetic order on the undoped ZnO thin films by inducing an alteration of electronic configuration.
ZnO-based dilute magnetic semiconductors (DMSs) have attracted intense interests due to their potential applications in spintronic devices . Room temperature (RT) ferromagnetism (FM) has been reported theoretically and experimentally in magnetic transition metal doped ZnO nanoparticles and thin films [2–7]. However, several works pointed out that the transition metal dopants are not essential in the observed ferromagnetism. For instance, the results of X-ray magnetic circular dichroism spectra showed that the magnetism in Mn doped ZnO nanoparticle and thin films is critically sensitive to defects other than the transition metal dopants themselves  and bulk ZnO doped with Co, Mn, or Cr shows paramagnetism [6, 9, 10]. Meanwhile, RT FM was observed in nonmagnetic ion doped ZnO thin films and nanoparticles [11–13] and even undoped ZnO films [14–17], nanoparticles [18, 19], or partially oxidized Zn nanowires [20, 21], which indicates that the RT FM observed in ZnO matrix may be intrinsic. It is restricted to some defect-rich regions, such as the surface, interface, and grain boundary, not uniform throughout the samples . On the other hand, the indirect exchange interaction models such as Zener/Ruderman-Kittel-Kasuya-Yosida (RKKY)-type exchange, double- and super-exchange, F-center-mediated bound magnetic polaron models, are hard to explain the observed RT FM induced by only few percent of magnetic ions. Thus, the intrinsic defects should be important on the FM order in ZnO-based DMSs. However, which kinds of defects play an important role, how the defects facilitate the magnetic coupling, and how to control these defects are still under intensive debate. Some reports demonstrated that RT FM could stem from the lattice defects such as oxygen vacancy () or Zn interstitial () in pure ZnO thin films, nanoparticles, and nanowires [17, 23–26]. Straumal et al.  demonstrated that FM only appears if the ratio of grain-boundary area to grain volume exceeds a certain threshold value. Sanchez et al.  predicted that varying the hydrogen density on the ZnO (0001) surface can achieve reversible switch of surface FM. More interestingly, even absorbing certain organic molecules can induce ferromagnetic-like behavior in undoped ZnO nanoparticles . These results challenge the understanding of the origin and mechanism of FM.
So far, although lots of works have been carried out to explore the origin of RT FM in undoped ZnO, the results are far from convincing and even some of the results are inconsistent, partly because ZnO is a semiconducting material with many species of native defects with quite a few of them behaving as shallow donors. Now, it is known that the native defects depend strongly on preparation methods and conditions. ZnO materials prepared by various methods from different groups generally show significant differences in physical properties including native defect/impurity species and density, mobility, and crystallinity. When these ZnO materials are employed for DMSs study, it is not a surprise that distinct results were reported even with similar conditions. Therefore, it is the most important to elucidate the effect of specific film-growth conditions. In this study, polycrystalline ZnO films were fabricated under different oxygen partial pressure (). The experimental results show that the only RT FM observed in ZnO film deposited under pure Ar and saturated magnetization is 0.89 emu/cc, while other samples deposited under Ar and O2 mixture are diamagnetism. After depositing a single Zn layer on the magnetic film and annealing the sample at high temperature, the saturated magnetization significantly increased to 1.62 emu/cc. These results suggest that the Zn interstitial may be a response to the origin of FM order in pure ZnO thin films.
A series of polycrystalline ZnO films were fabricated by RF-sputtering ZnO (99.99%) targets in Ar (99.999%) and O2 (99.999%) mixture at room temperature. The base pressure of the chamber was better than 1 × 10−5 Pa before deposition and the total pressure for sputtering was kept at 2.0 Pa. The RF-sputtering power of ZnO target was kept at 260 W. The films were deposited on glass and kapton substrates for the measurements of structural and transport properties, respectively. To eliminate the spurious magnetic data, the samples and polymer tweezers were cleaned with acetone prior to measurement. The films thickness was kept at 200 nm. The microstructure of the films was characterized by X-ray diffraction pattern (XRD) with Cu radiation () using X’ Pert PRO machine. The composition and chemical states of ZnO thin films were examined by X-ray photoelectron spectroscopy (XPS) and auger electron spectroscopy (AES) using Physical Electronic Spectrometry machine. The DC electrical resistivity measurements were measured using a conventional four-probe method performed in a Quantum Design PPMS. The magnetization measurements were carried out using a Quantum Design vibrating sample magnetometry.
3. Results and Discussion
Figure 1(a) shows the XRD pattern of the ZnO polycrystalline samples fabricated under different oxygen partial pressure (). The results indicate that all samples have highly (00l)-preferred orientation in contrast to the standard diffraction pattern of wurtzite ZnO. The particle size can be derived from the Scherrer formula : where is the particle size along () direction, is the full width at half maximum (FWHM) of the XRD peak, nm is the wavelength of Cu radiation, and is the Bragg angle. Figure 1(b) shows the relation between obtained particle size using the FWHM of (002) peaks and . It can be seen that there is not monotonic dependence of particle size on the . At low , the particle size increases with increasing , reaches the maximum value at = 1 Pa, and then decreases to 42.7(9) at = 1.5 Pa. With the increasing, the particle size of the ZnO thin films tends to be a constant.
The composition and chemical states of the ZnO thin films deposited under and are further investigated by XPS analysis. Samples were etched by Ar+ bombardment (5 × 105 Torr) for 5 min to examine the intrinsic chemical state of each element in the films. A broad scan survey spectrum indicates that only Zn, O, and C elements exist and no other detectable contaminated element above 0.1% exists in the ZnO samples. As shown in Figure 2(a) the peak positions of Zn and Zn are similar in both samples. Comparing the XPS standard spectra of Zn , it is concluded that the valence state of Zn element is +2. On the other hand, the peaks of Zn in both samples exhibit slight asymmetry. Islam group has analyzed the Zn peak of ZnO thin film systematically and attributed this kind of asymmetry of Zn peak to the existence of excess zinc in the films . No such asymmetry is observed for hydrogen-annealed pure ZnO films. But the exact nature of the distribution of Zn in the ZnO matrix remains under investigation. In order to confirm the existence of zinc in the films, AES measurements were carried out. Figure 2(b) presents a Zn(L3M45 M45) AES signal of the ZnO samples deposited under and . The major peaks at 264.2 eV are considered to be associated with Zn2+ in ZnO matrix. The minor one at 261.2 eV is due to Zn of metallic Zn or in ZnO matrix lattice. It can be seen that the peak intensity at 261.2 eV for the sample deposited under is significantly larger than that for sample prepared under . It implies that more metallic Zn or can be generated under oxygen-deficient atmosphere.
Deeper insight into the chemical states of oxygen is achieved through the analysis of the O 1s peaks of ZnO polycrystalline samples deposited under and , as shown in Figure 3. The broad and asymmetric O 1s peaks could be consistently fitted by a Gaussian function to separate the multicomponent oxygen species, which centered at eV, eV, and eV, respectively. The component on the low binding energy side of the O 1s at eV is attributed to O2− ions in wurtzite structure of hexagonal Zn2+ ion array, surrounded by Zn atoms with their full complement of the nearest neighboring O2− ions . In other words, the intensity of this component is the indicator of the amount of oxygen atoms in a fully oxidized, stoichiometric surrounding. The medium binding energy component at eV may partially be associated with O2− ions that are in oxygen-deficient regions within the matrix. Thus, the variation of the relative intensity ratio of medium component to total O 1s may be connected in part to the variations in the concentration of oxygen vacancies. It can be seen that this ratio for the sample prepared without O2 is remarkably larger than the sample deposited under . It is consistent with AES results of Zn; that is, without O2, more and appear when compared to the sample deposited under O2. Finally, the appearance of the high binding energy component at eV indicates the presence of loosely bound oxygen in the ZnO films belonging to specific species, such as adsorbed H2O or adsorbed O2, which is difficult to remove by just increasing during deposition process.
Figure 4 shows magnetization loops of ZnO films deposited under different . The applied magnetic field was parallel to the surface of the sample. The data in the main figure is curves before the subtraction of the diamagnetic signal of samples, which indicates the sample prepared under shows RT FM. Upper inset of Figure 3 obtained from subtracting the saturated linear parts of the measured signal shows typical hysteresis behaviors and the saturated magnetization is 0.89 emu/cc. However, other samples deposited under different oxygen partial pressure are diamagnetic, confirming that no FM impurities were introduced during the preparation of the films. It should be noted that FM behavior and average grains diameters upon different oxygen partial pressure have different trends. It implies that the average grains sizes are indirectly related to the FM in undoped ZnO films. On the other hand, the measured resistivity of the samples deposited under is Ω cm at RT.
Indeed, the origin of RT FM in undoped ZnO is still a controversial issue. Many hypotheses have been presented to give a reasonable interpretation for the origin of the RT FM in pure ZnO. Since the sample deposited under is insulators, the carrier-mediated RKKY-type model seems not to be applicable. According to previous work [23–26], the origin of the room temperature FM of undoped ZnO is due to the introduction of and/or defects rather than Zn vacancies (), because formation energy of is so high that it could not preferably form in ZnO. The chemical states of Zn and O ions in ZnO samples deposited under different show that and coexist in the as-deposited samples. As increases, both of the and are decreasing meanwhile the FM disappears at higher . Thus, the and/or should contribute to the origin of FM in pure ZnO thin films. To further confirm which kind of defect plays a more important role in the origin of FM in the sample, a layer of pure Zn with thickness of about 70 nm was deposited on the ZnO film deposited under . Then, the sample was heated in high vacuum at 300°C for 10 min. Because the diffusion of Zn is easier than that of oxygen  and there are not enough oxygen atoms from the air which can diffuse in the lattice to oxidize the diffused Zn, will generate and be trapped in the lattice, which leads to the increase in defect density of . On the other hand, magnetic measurement indicates that the saturated magnetization of annealed sample increases to 1.62 emu/cc. Thus, not should be responsible for the observed weak RT FM in as-deposited sample and the significant increase of in the annealed sample.
Theoretical calculation indicated that the level of lies close to the bottom of the conduction band (shallow donors), which will induce strong interaction between the localized interstitial Zn 4s level and the conduction band . This interaction alternates the electronic structure, leading to ferromagnetic-like behavior. It should be noted that this modification of the semiconductor electronic structure can be realized in the absence of the magnetic ions. More generally, other methods inducing such kind of shallow donors will also alternate the electronic structure and result in the RT FM, such as fabricating ZnO low dimensional nanoparticles with more intrinsic defects, capping with organic molecules into ZnO nanoparticle  and producing more defects by mechanical milling in ZnO nanoparticles .
In summary, RT FM is observed in undoped ZnO thin films deposited without oxygen, while other samples deposited under different are all diamagnetism. After depositing a single Zn layer on the magnetic ZnO thin films and annealing the sample at high temperature, the saturated magnetization significantly increased. All results indicate that the origin of FM order in pure ZnO films should be related to the defects. The shallow donor caused by defects might modify the electronic structure of undoped ZnO thin films, leading to the RT FM. Our result will help to get further insight into the ferromagnetic origin in undoped ZnO systems.
Conflict of Interests
The authors declare that there is no conflict of interests regarding the publication of this paper.
This work was supported by the National Natural Science Foundation of China (Grant nos. 51102075, 51171056, and 51371075) and the Key Project of Science and Technology for Colleges in Hebei Province, China (Grant no. ZD2010120).
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