# Influence of Fe-Doping on the Structural and Magnetic Properties of ZnO Nanopowders, Produced by the Method of Pulsed Electron Beam Evaporation

Authors: V. G. Il’ves; S. Yu. Sokovnin; A. M. Murzakaev
Journal: Journal of Nanotechnology
 (2016)

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## Abstract

The nanopowders (NPs) ZnO-Zn-Fe and ZnO-Fe with the various concentrations of Fe (x
F
e) (0
≤
x
F
e
≤
0.619 mass.%) were prepared by the pulsed electron beam evaporation method. The influence of doping Fe on structural and magnetic properties of NPs was investigated. X-ray diffraction showed that powders contain fine-crystalline and coarse-crystalline ZnO fractions with wurtzite structure and an amorphous component. Secondary phases were not found. The magnetic measurements made at room temperature, using the vibration magnetometer and Faraday’s scales, showed ferromagnetic behavior for all powders. Magnetization growth of NPs ZnO-Zn and ZnO-Zn-Fe was detected after their short-term annealing on air at temperatures of 300–500°C. The growth of magnetization is connected with the increase in the concentration of the phase ZnO with a defective structure as the result of oxidation nanoparticles (NPles) of Zn. The scanning transmission electron microscopy (STEM) showed a lack of Fe clusters and uniform distribution of atoms dopant in the initial powder ZnO-Zn-Fe. A lack of logical correlation between magnetization and concentration of a magnetic dopant of Fe in powders is shown.


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## Body

## 1. Introduction

The diluted magnetic semiconductors (DMS) cause a great interest due to their potential use in spintronics devices [1–4]. Materials of spintronics have to be steady against the influences of normal environment (to pressure, temperature, and humidity), in order to be integrated with elements of modern silicon electronics; the time of spin coherence should not be too short (>100 ns), to possess high mobility of charge carriers and to be ferromagnetic at room temperature [5]. The active search of ferromagnetic nanostructured DMS is considered to be the most attractive since the semiconductor nanostructuring allows for increase of solubility of transitional metal impurity in its crystal lattice to desirable level of 1-2% for providing the magneto ordered condition and suppresses the undesirable aggregation of impurity in clusters. It is expected that the nanostructured materials at temperature of Curie will be significantly higher than in volume materials [5–8].Now there is no theory explaining the nature of ferromagnetism in the various DMS [9, 10] types and ambiguity of experimental data. In many works there is an indication of a lack of logical correlation between magnetization of DSM and concentration of a magnetic dopant [11–13]. Often, the ferromagnetic response of undoped materials (so-called d0-ferromagnetism) surpasses the corresponding response in doped materials by magnetic 3D elements semiconductors and oxides [14–19]. There are not yet enough studies in which the investigated materials with concentrations of magnetic dopants below a percolation threshold have been observed.It should be noted that direct exchange interaction cannot result in ferromagnetism of DMS since the distance between the neighboring magnetic ions is rather great for their electron shells to be overlapped. Therefore research into the nature of ferromagnetic ordering in DMS at the expense of indirect exchange interaction via carriers of charge is actual [5, 20].Z
n
1
-
x
F
e
x
O ferromagnetic semiconductors with a temperature of Curie higher than the room were performed using the sol-gel method [21], solid-state reaction route [22, 23], magnetron sputtering [24], and a number of other methods.For the synthesis of nanoparticles ZnO-Fe a spherical crushing (ball milling) [25, 26] was used along with the sol-gel method [27–31], codeposition [32–35], pulsed laser deposition [36], burning of solutions [37], microwave synthesis [38], flame spray pyrolysis [39, 40], chemical pyrophoric reaction method [41], the method of autocombustion [42], and so forth.The analysis of literature showed that irrespective of a method for obtaining nanoparticles and a type of the nanostructured material (thin films, nanopowders, nanostructures with various morphologies, nanorods, nanowires, nanodisks, nanotetrapods, etc.) in ZnO-Fe system general regularities are observed: with the growth of Fe dopant concentration the size of nanoparticles, crystallinity, and width of the bandgap zone decrease [28, 32, 33, 40, 43, 44]; when annealing samples with concentration of Fe dopant from 2–5 mass.% and above, with the growth of annealing temperature the formation of the secondary phase-spinel ZnFe2O4 dominates [23, 27, 42, 43, 45, 46]. The formation of other secondary phases, Fe3O4 [47] and α-Fe [48], was observed. More often the mixed valency of dopant ions (Fe2+ and Fe3+) was reported in the final product [23, 28, 46, 48, 49].At the concentration of Fe in ZnO-Fe system higher than 1 at.%, magnetization of samples usually changes linearly (grows [35, 37, 44, 50] or decreases [24]) with increase of dopant concentration [23, 28, 35, 51] up to the moment of emergence secondary phases. However, at a lower level of doping (less than 1 at% Fe), a nonlinear course of dependence magnetization was noted from Fe concentration [38].The general tendency in change of magnetization in the ZnO-Fe system with growth of dopant concentration is the strengthening of paramagnetic contribution to total magnetization (the curve of magnetization does not reach saturation even in big magnetic field ±50 kOe). Note the considerable dispersion in absolute magnitudes of magnetization in the various nanomaterials ZnO-Fe and big variations of solubility limit of Fe in ZnO lattice (from 1 [23] up to 21 [33] mass. Fe%) which depend on the methods and conditions of synthesis samples ZnO-Fe [10]. In particular, in [52] it was shown that ZnO sample with 1% Fe shows diamagnetic behavior though samples from 2 and 3% Fe show the ferromagnetic nature, and samples with higher doping level of Fe show paramagnetism; in [22] NPs Z
n
1
-
x
F
e
xO (x
=
0.02, 0.04, 0.06, 0.08, 0.10), received by the sol-gel method, show the room temperature ferromagnetism (RTFM) at 2% Fe; other NPs (concentration of Fe x
F
e
≥
4%) show paramagnetic properties.The strengthening ferromagnetism in Fe-doped ZnO when annealing samples in a reduced atmosphere of Ar/H2 (5%) was documented [21]. Research of aging nanoparticles of ZnO and ZnO-Fe (the forced hydrolysis) showed considerable degradation of ferromagnetic properties. Unusual growth of nanoparticles ZnO and ZnO-Fe prepared by method of forced hydrolysis and easing of their ferromagnetic properties within 1–4 years was observed thanks to aging in the environment (the size of particles in sample of Zn0.95Fe0.05O changed from 7.9 nm to 9.0 nm, and magnetization decreased with 1
∗
10
-
3 to 2
∗
10
-
4 emu/g) as shown in work [34]. The temporary instability of powders partly can be one of sources of divergence of experimental data in literature.In samples of ZnO, doped with various 3D elements, antiferromagnetism [53, 54], spin-glass behavior [52, 55], and paramagnetism were observed [56, 57]. These supervisions indicate a strong dependence of RTFM on conditions of preparation samples DSM [10]. In separate messages there was a very low temperature of magnetic ordering specified in such systems [58].Thus, the situation with existence and explanation of RTFM nature in ZnO-Fe system is very ambiguous.The purpose of these efforts is to investigate the influence of structural defects on the magnetic properties of nanopowders ZnO-Fe received by pulsed electron beam evaporation [59, 60], at the small concentration of magnetic dopant Fe (less than 1 mass.%).


## 2. Experiments

The ZnO-Zn-Fe and ZnO-Zn NPs were deposited on glass substrates by pulsed electron beam evaporation at the “Nanobeam-2” installation [59, 60], in vacuum (the operation pressure was 4 Pa). During the deposition, the temperature of substrates was approximately 100−200°C. Ceramic targets with nominal composition ZnO-(1-3-5 mass%) Fe2O3 were fabricated by a standard solid state reaction method. Appropriate proportions required for ZnO-(1-3-5%) Fe2O3 were mixed by manual grinding according to the desired stoichiometry and pelletized, sintered at 1000°C for 1 hour.The mode of evaporation was as follows: an accelerating voltage of 40 kV, an electron beam current of 0,4 A, pulse length of 100μs, pulse repetition rate of 100 Hz, scanning area of the electron beam on the target of 2,5 sm2, and time of evaporation of 30 min. All nanopowders had black color. After annealing in air NPs were changed to a white-grey color due to oxidation of Zn nanoparticles (NPles).The percentages of Fe in the samples were checked by a iCAP 6300 ICP spectrometer and energy-dispersive X-ray spectroscopy (EDX). The crystal structure of theZ
n
1
-
x
F
e
x
O (x
=
0.0061) was characterized by Shimadzu X-ray diffractometer XRD-7000 with nickel-filtered Cu Kα radiation. The specific surface area of powders (S
B
E
T) was determined by the Brunauer-Emmett-Teller (BET) method on a Micromeritics TriStar 3000 setup.Thermograms and the mass spectra of the samples were recorded with differential scanning calorimetry (DSC) and thermogravimetry (TG) using an STA_409_PC Luxx synchronous thermoanalyzer, coupled with a QMS_403C mass spectrometer (resolution 0.5 amu, Scan, Scan_Bargaph, MiD) from NETZSCH.


## 3. Results and Discussion

### 3.1. Structural and Element Analysis of Nanopowders

Results ofS
B
E
T measurement and the chemical analysis (ICP method) of NPs ZnO, ZnO-Zn, and ZnO-Zn-Fe are given in Table 1. From Table 1, it is visible that the Fe mass content in NP ZnO-Zn-Fe does not exceed 1 mass.% and also does not depend linearly on Fe mass content in precursors (targets). S
B
E
T of NP ZnO-Zn-Fe does not exceed 45 m2/g. Decrease in S
B
E
T NP with x
F
e growth in targets is caused by strengthening of adhesion NP to glass substrates and formation of coatings on the surface of substrates. Dependence between a mass content of x
F
e dopant and S
B
E
T of NPs is close to the linear.Table 1
Specific surface area (S
B
E
T) and the iron concentration (x
F
e) in NPs.
Sample number
Target composition (pressure О2)
S
B
E
T, m2/g
x
F
e, mass.% (ICP)
1
ZnO-1 wt.% Fe2O3
44,87
0,128 ± 0,010
2
ZnO-3 wt.% Fe2O3
5,23
0,619 ± 0,025
3
ZnO-5 wt.% Fe2O3
13,66
0,569 ± 0,023
4
ZnO-Zn (4 Pа)
17
—
5
ZnO (20 Pа)
12,5
—
6
ZnO (45 Pа)
24,5
—Previously, in many works [61] it was specified that when using gas-phase methods for producing NPs, irrespective of Fe mass content in targets, the mass content of x
F
e dopant in the final product does not exceed 1 mass% that will be coordinated in relation to ours by results.In Table2 parameters of lattices, relative concentration of crystal phases, and the size of particles are specified in NPs. Essential influence on NP properties puts oxygen pressure in the evaporation camera. With an oxygen pressure in the vaporizing camera of equal (20–50) Pa there was a formation of NP pure ZnO white color. Synthesized NP contained (10–17) mass.% of coarse-crystalline fraction (CC) ZnO and (59–83) mass.% of fine-crystalline fraction (FC) ZnO. In all NPs the amorphous phase is found, from trace amounts to a few percents.Table 2
Relative concentrations of the crystalline phases, average values of coherent scattering regions (CSR) in NPs, and lattice parameters of crystalline phases ZnO.
Sample (pressure)
ZnO (CC)
ZnO (FC)
Zn
Lattice parameter ZnO (FC), Å
Сoncent., wt.%
CSR, nm
Сoncent., wt.%
CSR, nm
Сoncent., wt.%
CSR, nm
ZnO-Zn-Fe
x
F
e = 0,619
17
>200
59
≈3
24%
4,1
a
=
3
,
239
±
(
4
)
c
=
5
,
221
±
(
9
)
ZnO-Zn
9
>200
57
≈3
34
10
a
=
3
,
244
c
=
5
,
246
ZnO (20 Pа)
—
—
>95
14,2 ± 1,3
—
—
a
=
3
,
2535
±
(
8
)
c
=
5
,
2252
±
(
30
)
ZnO (50 Pа)
17
≈100
83
≈8,3
—
—
a
=
3
,
245
c
=
5
,
223
ZnO-target
a
=
3
,
25
c
=
5
,
209
ReferencestandardPDF-200-001-1136
a
=
3
,
25
c
=
5
,
21Particles of the CC ZnO can be removed from NPs by means of sedimentation in a liquid phase [60] (e.g., a sedimentary sample of ZnO (20 Pa), Table 2).NPs ZnO-Zn and ZnO-Zn-Fe included a significant amount of metal nanoparticles Zn formed as a result of decomposition ZnO at high temperature of evaporation in vacuum and had black color. There was a reduction of the FC size of the phase ZnO as in doped and undoped NPles from 14,3 nm to 3-4 nm (Table2) and considerable change of crystal lattice parameters. The broadening and shift of diffraction peaks in area of small corners in NP ZnO-Zn-Fe indicate replacement of ions of Zn2+ (ionic radius 0,74 Å) in ZnO lattice by Fe2+ ions (ionic radius 0,77 Å). If the trivalent ion of Fe3+ is built in knots of wurtzite lattice, replacing zinc ions, the parameter of cell has to decrease since for tetrahedral environment the radius of ion of Fe3+ is equal to 0,67 Å.However, we observed significant increase in parameter from wurtzite lattice of FC ZnO in the undoped samples received in the oxygen-containing atmosphere with various pressures (5,2252 Å (20 Pa) and 5,223 Å (50 Pa)) and in NP ZnO-Zn received in vacuum (5,246 Å). The parameter growth with FC ZnO of undoped samples indicates considerable stretching of lattice of samples because of inevitable formation of oxygen vacancies at evaporation in deficiency of oxygen.In works [61–64] it is shown that Fe ions in nanomaterials (thin films, various nanostructures, nanopowders, etc.) on the basis of ZnO-Fe can be in two- or three-valent condition separately, and in the mixed valent condition, depending on the method and conditions of producing materials. In our case, proceeding from the above changes of crystal structure of NP ZnO-Zn-Fe concerning structure of volume ZnO, there was a formation of solid solution of an oxide of FeO iron in ZnO on the replacement mechanism; that is, Fe2+ ions were positioned in regular tetrahedral positions of wurtzite lattice.In Figure2 SEM/TEM pictures of particles submicronic powder (target) ZnO and NPs ZnO-Zn and ZnO-Zn-Fe produced by electron beam evaporation in oxygen (20 Pa) and vacuum are given.In the submicronic powder ZnO (pure for analysis) of which targets are made, significant amount of perfect crystalline nanostructures (nanotetrapods, nanorods, etc., Figure2(a)) is revealed. Narrow, high intensity peaks on XRD pattern of submicronic powder (Figure 1(a)) also confirm its high crystallinity. In Figures 2(b)–2(d) it is visible that all NPs formed during electron evaporation had similar morphology and consisted of the agglomerated NPles with the shape close to spherical, up to 10–20 nm in size; thus agglomerates were of the nano- and submicronic sizes. Note the existence of significant amount of amorphous particles of an arbitrary shape (Figure 2(d)) and separate core-shell particles (inserts in Figure 2(b) and Figure 2(c)) in NPs.Figure 1
XRD pattern of (a) ZnO submicron powder, (b) ZnO nanopowder (Po
2 = 45 Pa), (c) NP ZnO-Zn, and (d) NP ZnO-Zn-Fe (x
F
e = 0.619 wt %).Figure 2
(a) SEM picture of particles of submicronic powder (target) ZnO (designation: T, nanotetrapods; R, nanorods); (b) TEM NP ZnO-Zn picture (on the insert, core-shell nanoparticle ZnO with amorphous shell); (c) TEM picture NP ZnO-Zn-Fe (on the insert, the electron diffraction pattern from the amorphous area of sample); (d) TEM picture of agglomerate nanoparticles ZnO-Zn-Fe (on the insert, the electron diffraction pattern from the crystalline area of sample).
(a)
(b)
(c)
(d)Quantitative EDX analysis from several local areas of sample ZnO-Zn-Fe (x
F
e
=
0.619 mass.%, ICP) showed considerable dispersion on concentration of Fe (from 0.17 up to 3 mass. Fe%) and lack of other impurity elements in sample. Results of EDX analysis from sample area (it is shown on Figure 3 insert) by ZnO-Zn-Fe are given in Figure 3. Red color shows spectral lines from the copper grid.Figure 3
EDX spectra of sample ZnO-Zn-Fe (x
F
e
=
0.619 mass.% (ICP)).Distribution of elements O, Fe, and Zn on several areas of the sample ZnO-Zn-Fe (Figure4(a)) is qualitatively estimated by means of EDX mapping by the STEM method (Figures 4(b)–4(d)). Mapping showed uniform distribution of atoms O and Zn. However, distribution of atoms Fe (Figure 4(d)) is less uniform. In Figure 4(d) the tendency to formation of curved “chains” atoms can be observed. Formations of visible congestions from atoms Fe (Fe clusters) are not observed. In Figure 4(e) there is EDX range of the sample ZnO-Zn-Fe where it is presented that the sample generally contains atoms Zn and O, with trace quantity (and trace) of the Fe element. On an insert of Figure 4(e) it is shown that the concentration of Fe in this sample was about 0.17 mass.%.Figure 4
(a) STEM image of ZnO-Zn-Fe sample; (b), (c), (d) the corresponding EDX mappings of O, Zn and Fe; (e) EDX spectra of sample ZnO-Zn-Fe.
(a)
(b)
(c)
(d)
(e)


### 3.2. Magnetic Properties and Phase Transformations of NPs

For the purpose of receiving NPs ZnO-Zn with the minimum content of parasitic impurity, we carried out powder deposition on a glass substrate. Target material from the submicronic powder ZnO previously was checked on Faraday’s scales. Results of measurements showed the existence of weak ferromagnetic response in submicron powder (1,5
∗
10
-
3 emu/g) connected, either with impurity or with presence at powder quantity of perfect nanostructures (nanotetrapods and nanorods, Figure 2(a), are shown by shooters) which, as we know, possess their own RTFM [35, 41, 43].The increased magnetization of NP ZnO-Zn besieged on metal substrates most likely was caused by the impurity formed in powders owing to the reverse diffusion of substrates elements at high-temperature deposition.Curves of magnetization (M) are given in Figure 5 at the room temperature for NP ZnO-Zn (34 mass.% Zn) from a glass substrate in a magnetic field 12 kOe.Figure 5
Room temperatureM
-
H curves for ZnO-Zn NP: (1) as prepared and (2) after annealing.NP ZnO-Zn showed a weak ferromagnetic response at room temperature, equal to7
∗
10
-
3 emu/g.The growth of magnetization of sample ZnO-Zn after short-term annealing in the air atmosphere (temperature of annealing of 300°C, time of annealing of 30 min.) appeared to be unexpected; magnetization of the annealed sample grew to 9,5
∗
10
-
3 emu/g.Note that the growth of magnetization NPles of pure ZnO after annealing in the oxidizing atmosphere is observed in work [65]; the growth of magnetization is explained with formation of clusters from oxygen vacancies. In our case, it is the most probable that the growth of magnetization was caused by a process of phase transformation (oxidation) of NPles Zn in ZnO oxide when annealing. Considering the small duration and low temperature of annealing, we do not exclude that the process of oxidation Zn to ZnO took place not completely that could lead to formation of some quantity of core-shell structures of ZnO-Zn (a diamagnetic core from Zn and a shell from amorphous ZnO). The example such of a core-shell structure in NP ZnO-Zn is shown on Figure 2(b) insert. It is probable that the process of oxidation of NPles Zn and forming of core-shell structures leads to increase of the concentration of oxygen vacancies in the annealed sample that was reflected in magnetization growth.Note the increase of diamagnetic contribution to the specific magnetization of sample ZnO-Zn in magnetic field higher than 7 kОe. Thus, strengthening of magnetization NP ZnO-Zn after annealing can be caused by a number of factors: formation of amorphous layers on borders between ZnO nanoparticles, generation of core-shell structures with the broken stoichiometry on the interface between core and shell, and clustering of oxygen vacancies.In particular, emergence of ferromagnetic properties in films of pure ZnO at the expense of formation of foam-like grid from amorphous ZnO between NPles is shown in Straumal’s numerous works [11] and correlates with our data.Besides, the number of experimental works accruing every year much more confirms that carriers of a charge are not so necessary for RTFM emergence; in particular, ferromagnetic interaction is observed in films without free carriers in a dielectric condition [10, 66–71]. In our case, after annealing of conducting NP ZnO-Zn as a result of oxidation of NPles Zn the number of free carriers sharply decreased (powder turned into dielectric) that directly correlates with conclusions [10, 66–71]. The growth of magnetization of NP ZnO-Zn after annealing proves that the role of free carriers in RTFM formation in annealed NP ZnO-Zn is insignificant. Note works [72, 73] where the inverse correlation between magnetization and electronic density was shown.In Figure6 magnetization curves are given at the room temperature of NP ZnO-Zn-Fe (x
F
e
=
0.128, 0.569, 0.619 mass.%) in a magnetic field 12 kOe [59].Figure 6
Magnetization change at room temperature in NP ZnO-Zn-Fe in relation to concentration of Fe.From Figure6 it follows that dependence of the magnetic moment on atom of Fe (μ
B/Fe) from x
F
e in NP ZnO-Zn-Fe is nonlinear. The maximum magnetic moment (0,272 μ
В/Fe) is determined in NPs at an intermediate concentration of x
F
e
=
0,569 mass.% that confirms, noted above, lack of direct correlation between magnetization and concentration of iron magnetic ions in powders and will be coordinated with conclusions [10–13, 71].In particular, authors of the work [11] connect ferromagnetism of ZnO not with entered ions of transitional metals but with the magnetic moments in vacancies of lattice which concentrate on borders of grains. Therefore, the introduction of ions Fe probably only promotes emergence (strengthening) of ferromagnetism in NP ZnO-Zn-Fe due to emergence of noncoupled spins Fe2+(Fe3+) ions and to increase in disorder and defectiveness of NP structure at doping (that confirms corresponding change of ZnO-Zn-Fe lattice parameters).Further increase in concentration of Fe in NP ZnO-Zn-Fe with 0,569 up to 0,619 mass.% led to decrease in magnetic response. Decrease in magnetization shows that magnetization of NP is not connected with possible formation of secondary phases and type of clusters Fe, Fe3O4, or γ-Fe2O3. If pure Fe or its oxides were responsible for ferromagnetic behavior of NP, the increase in concentration of x
F
e in samples would lead to an increase in a volume fraction of these phases in samples and the related magnetic response.Magnetization curves of samples withx
F
e
=
0,569 and 0,619 mass.% did not reach saturation in the magnetic field to 12 kOe. That points at strengthening of paramagnetic contribution to magnetization. Strengthening of antiferromagnetic interaction between the neighboring Fe-Fe ions suppresses ferromagnetism at high concentration of Fe. In particular, the similar behavior was traced in ZnO-Fe NPles in [74], where with x
F
e growth up to 20 at.% the increase of paramagnetic contributionoccurred. Note that, in [74] with the comparable sizes of particles, our NPles had magnetization of nanoparticles 10 times less which can be explained by smaller concentration of the defects formed during the chemical method.It is known [75] that creation of effective exchange interaction between magnetic ions in DMS requires rather high concentrations of dopant (usually units%), with rare exception [10, 76]. In our NPs concentrations of magnetic dopant were 10 times less than the threshold that directly specifies that the mechanism of observed ferromagnetism is not defined by short-range exchange interaction between magnetic ions of dopant, improbable because of long distances between ions, and is more connected with defects of various types which were formed in NPles as a result of nonequilibrium crystallization of NPles with high temperature on cold glass substrates.In addition, the question of the ferromagnetism nature in heterophase NP ZnO-Zn-Fe complicates the existence of amorphous components in NP detected from XRD and the microscopic analysis. Influence of dimensional factor on magnetization of NPs from the fine-crystalline phases ZnO and Zn is not excluded.After annealing of the conductive ZnO-Zn-Fe nanopowder, as a result of the oxidation of Zn nanoparticles the powder transformed into a dielectric. In such NPs density of electric carriers is low that excludes a possible explanation of ferromagnetism in NPs ZnO-Fe using the carrier-mediated exchange mechanism.In Figure7 magnetization curves of NPs ZnO-Fe (x
F
e
=
0.128, 0.569, 0.619 mass.%), received on the vibration magnetometer in magnetic fields ±1 T are given at the room temperature. Note the considerable strengthening of samples ZnO-Fe magnetization in comparison with magnetization of nonannealed NPs ZnO-Zn-Fe. Magnetization of samples with concentration of x
F
e
=
0.128, 0.569, 0.619 mass.% grew by ≈ 5, 2.5, and 2 times, respectively. Strengthening of magnetization of undoped sample ZnO-Zn after annealing (Figure 4) was much less (35%) that is possible to explain with non-full oxidation of NPles Zn to ZnO at lower temperature of annealing (300°C) and small time of annealing (30 min.).Figure 7
M versus H curves for ZnO-Zn-Fe NPs with various doping concentrations.Note that the magnetization of our samples is 10 times more than magnetization of samples ZnO-Fe with close concentration of dopant (≤1%) received with use of traditional ceramic synthesis (x
F
e of = 1%, M
S = 1,25
∗
10
-
2 emu/g, [42]), method sol-gel [28]) that obviously points to a defining role of structural defects on strengthening of ferromagnetic response and preference of use of strongly nonequilibrium methods for formation of structural defects in various materials, before methods of wet chemistry.The general nature of magnetization change of samples ZnO-Fe from a concentration of Fe remained the same, as with nonannealed samples of ZnO-Zn-Fe. All samples of ZnO-Fe showed RTFM and had well-defined hysteresis with coercive force in the range from 160 to 380 Oe. Thus, the sample withx
F
e
=
0.128% was completely saturated in the magnetic field ±1 T though curves magnetizing is exemplary with x
F
e
=
0.569 and 0.619 continued to grow with increase in the magnetic field and did not come for saturation. Similar change of magnetization curves with growth of a dopant concentration quite often has been observed in ZnO-Fe system before [28, 77, 78]. Note that the hysteresis loop measured on the ZnO-Fe sample (0.128%) is thinner than those measured on the other samples.The broadening of hysteresis loops is caused by the fact that with the growth of dopant concentration the average distance between ions of Fe decreases (see Table2) and antiferromagnetic exchange energy of ions Fe becomes less than ferromagnetic exchange energy; therefore the magnetic moments of ions Fe are ordered antiferromagnetically that reduces magnetism of samples [79].Now, in the theory of ferromagnetism DSM two models [10] connected with a charge transfer and with the formation of the connected magnetic polarons dominate.The ferromagnetism nature in NPs ZnO-Fe received can be explained using the model of the connected magnetic polarons [80].Polarons are in a low-doped sample (0.128% of Fe) at rather long distances from each other to carry out strong exchange interaction. Apparently, in a sample with a concentration of dopant of equal 0.519 mass.%, the distance between the neighboring polarons decreases and becomes optimum; therefore, the exchange between two neighboring magnetic polarons amplifies. It is possible that in a more strongly doped sample (x
F
e
=
0.619) the magnetic moment quickly decreased due to strengthening of dopant-dopant associations that brought progressive reduction of the orbital moment. Reduction of the magnetic moment in NPs ZnO-Fe with the growth of concentration Fe also indirectly confirms lack of the secondary magnetic phases Fe in the sample and is consistent with the XRD data. Consider the following:(A)
Similar picture of magnetization strengthening samples after annealing as in NPs ZnO-Zn and ZnO-Zn-Fe, observed earlier in ZnO-Zn-Cu system (300°C, time of annealing of 30 minutes) [81].
(B)
Magnetization growth in undoped Fe NPs ZnO-Zn and ZnO-Zn-Cu (the content of Fe impurity in the above samples according to ICP of the analysis did not exceed10
-
3
–
10
-
2 mass. Fe % that is 1-2 orders less than concentration of ions Fe in NPs ZnO-Fe (ZnO-Zn-Fe) directly specifies that the ferromagnetic response is not connected with magnetic ions Fe.
(C)
It is the most probable that, when annealing NPs ZnO-Zn and ZnO-Zn-Cu as the result of NPles Zn oxidation to NPles ZnO, recrystallization of NPles, partial crystallization of amorphous fraction, generation of core-shell structures (the core-Zn, the shall-ZnO), the concentration of various structural defects (oxygen vacancies, cation vacancies, interstitial atoms, dislocation, etc.) in NPs changed in a complex manner, which led to strengthening of magnetization samples.Dynamic heating of sample ZnO-Zn-Fe in the air atmosphere using the DSC-TG method also showed (Figure 8(b), curve TG) that full oxidation of nanoparticles Zn comes to the end at temperature ≈ 600°C that in addition confirms the possibility of preservation of core-shell structures in powder at short-term annealing at the temperature of 500°C.Figure 8
Heating thermograms DSC-TG and the mass spectra H2O and CO2 of the NPs ZnO-Zn (a) and ZnO-Zn-Fe (b).
(a)
(b)Oxidation of NPles Zn in NP ZnO-Zn-Fe began from temperature ≈ 200°C (exothermic peak 1 at curve TG in Figure8(b)) which is slightly higher than the temperature of the oxidation beginning NP ZnO-Zn equal to 110°C (Figure 8(a), curve TG). Thus, Fe introduction in ZnO inhibits temperature of the oxidation beginning of NPles Zn and reduces the speed of oxidation reaction NPles Zn in doped powder. Oxidation of NPles Zn comes to the end in NP ZnO-Zn (curve TG, Figure 8(a)) and ZnO-Zn-Fe (curve TG, Figure 8(b)) at temperatures of ≈280°C and 600°C, respectively.In our opinion, the new model of ferromagnetism is the most suitable one for an explanation of the nature of RTFM in systems ZnO-Zn and ZnO-Zn-Fe (Cu) in the diluted magnetic oxides (charge-transfer ferromagnetism model), offered by Coey et al. [82] which is based on the Stoner type of ferromagnetism connected with electrons in percolation defective structures, such as the grain boundaries.This model has successfully been applied to an explanation of ferromagnetic interaction in NPles of semiconductor oxides and doped ions of transitional metals in the mixed valent state [10, 83]. In particular, charge-transfer ferromagnetism model has been used for RTFM explanation in objects films of Z
n
x
Z
n
O
1
-
x close to our NP [84] and core-shell Zn/ZnO [85] structures. Besides the model does not assume homogeneous distribution of magnetic dopant on the sample that in the best way approaches the situation (Figure 4(c)).Thus, we showed that magnetism of low-doped (x
F
e
≤
0,619 wt.%) and undoped Fe NPs on the basis of ZnO is their intrinsic property. The dominating contribution to ferromagnetism of samples is made by various structural defects (oxygen vacancies, interstitial atoms of introduction, and amorphous component), instead of charge carriers.It is determined that there is nonlinear dependence of magnetization on concentration of magnetic dopant in NP ZnO-Zn-Fe and ZnO-Fe. The maximum magnetic moment in samples of ZnO-Zn-Fe and ZnO-Fe is observed at concentration of magnetic dopant equal to 0,519 wt.% which is much lower than a percolation threshold.The received results will be coordinated with Pan et al. [10] given the review where it is shown that the maximum magnetic moment in ZnO-Fe systems (Cu, Cr, Ni) is usually observed at concentration of dopant ≈ 1 аt.%. However, further work on ferromagnetism studying of the zinc oxide alloyed by Fe is required. It will be oriented to the establishment of an unambiguous correlation between defectiveness of structure and magnetic properties and the identification of defects in their nature and the mechanism of their interaction leading to the emergence of ferromagnetism at the room temperature.


## 3.1. Structural and Element Analysis of Nanopowders

Results ofS
B
E
T measurement and the chemical analysis (ICP method) of NPs ZnO, ZnO-Zn, and ZnO-Zn-Fe are given in Table 1. From Table 1, it is visible that the Fe mass content in NP ZnO-Zn-Fe does not exceed 1 mass.% and also does not depend linearly on Fe mass content in precursors (targets). S
B
E
T of NP ZnO-Zn-Fe does not exceed 45 m2/g. Decrease in S
B
E
T NP with x
F
e growth in targets is caused by strengthening of adhesion NP to glass substrates and formation of coatings on the surface of substrates. Dependence between a mass content of x
F
e dopant and S
B
E
T of NPs is close to the linear.Table 1
Specific surface area (S
B
E
T) and the iron concentration (x
F
e) in NPs.
Sample number
Target composition (pressure О2)
S
B
E
T, m2/g
x
F
e, mass.% (ICP)
1
ZnO-1 wt.% Fe2O3
44,87
0,128 ± 0,010
2
ZnO-3 wt.% Fe2O3
5,23
0,619 ± 0,025
3
ZnO-5 wt.% Fe2O3
13,66
0,569 ± 0,023
4
ZnO-Zn (4 Pа)
17
—
5
ZnO (20 Pа)
12,5
—
6
ZnO (45 Pа)
24,5
—Previously, in many works [61] it was specified that when using gas-phase methods for producing NPs, irrespective of Fe mass content in targets, the mass content of x
F
e dopant in the final product does not exceed 1 mass% that will be coordinated in relation to ours by results.In Table2 parameters of lattices, relative concentration of crystal phases, and the size of particles are specified in NPs. Essential influence on NP properties puts oxygen pressure in the evaporation camera. With an oxygen pressure in the vaporizing camera of equal (20–50) Pa there was a formation of NP pure ZnO white color. Synthesized NP contained (10–17) mass.% of coarse-crystalline fraction (CC) ZnO and (59–83) mass.% of fine-crystalline fraction (FC) ZnO. In all NPs the amorphous phase is found, from trace amounts to a few percents.Table 2
Relative concentrations of the crystalline phases, average values of coherent scattering regions (CSR) in NPs, and lattice parameters of crystalline phases ZnO.
Sample (pressure)
ZnO (CC)
ZnO (FC)
Zn
Lattice parameter ZnO (FC), Å
Сoncent., wt.%
CSR, nm
Сoncent., wt.%
CSR, nm
Сoncent., wt.%
CSR, nm
ZnO-Zn-Fe
x
F
e = 0,619
17
>200
59
≈3
24%
4,1
a
=
3
,
239
±
(
4
)
c
=
5
,
221
±
(
9
)
ZnO-Zn
9
>200
57
≈3
34
10
a
=
3
,
244
c
=
5
,
246
ZnO (20 Pа)
—
—
>95
14,2 ± 1,3
—
—
a
=
3
,
2535
±
(
8
)
c
=
5
,
2252
±
(
30
)
ZnO (50 Pа)
17
≈100
83
≈8,3
—
—
a
=
3
,
245
c
=
5
,
223
ZnO-target
a
=
3
,
25
c
=
5
,
209
ReferencestandardPDF-200-001-1136
a
=
3
,
25
c
=
5
,
21Particles of the CC ZnO can be removed from NPs by means of sedimentation in a liquid phase [60] (e.g., a sedimentary sample of ZnO (20 Pa), Table 2).NPs ZnO-Zn and ZnO-Zn-Fe included a significant amount of metal nanoparticles Zn formed as a result of decomposition ZnO at high temperature of evaporation in vacuum and had black color. There was a reduction of the FC size of the phase ZnO as in doped and undoped NPles from 14,3 nm to 3-4 nm (Table2) and considerable change of crystal lattice parameters. The broadening and shift of diffraction peaks in area of small corners in NP ZnO-Zn-Fe indicate replacement of ions of Zn2+ (ionic radius 0,74 Å) in ZnO lattice by Fe2+ ions (ionic radius 0,77 Å). If the trivalent ion of Fe3+ is built in knots of wurtzite lattice, replacing zinc ions, the parameter of cell has to decrease since for tetrahedral environment the radius of ion of Fe3+ is equal to 0,67 Å.However, we observed significant increase in parameter from wurtzite lattice of FC ZnO in the undoped samples received in the oxygen-containing atmosphere with various pressures (5,2252 Å (20 Pa) and 5,223 Å (50 Pa)) and in NP ZnO-Zn received in vacuum (5,246 Å). The parameter growth with FC ZnO of undoped samples indicates considerable stretching of lattice of samples because of inevitable formation of oxygen vacancies at evaporation in deficiency of oxygen.In works [61–64] it is shown that Fe ions in nanomaterials (thin films, various nanostructures, nanopowders, etc.) on the basis of ZnO-Fe can be in two- or three-valent condition separately, and in the mixed valent condition, depending on the method and conditions of producing materials. In our case, proceeding from the above changes of crystal structure of NP ZnO-Zn-Fe concerning structure of volume ZnO, there was a formation of solid solution of an oxide of FeO iron in ZnO on the replacement mechanism; that is, Fe2+ ions were positioned in regular tetrahedral positions of wurtzite lattice.In Figure2 SEM/TEM pictures of particles submicronic powder (target) ZnO and NPs ZnO-Zn and ZnO-Zn-Fe produced by electron beam evaporation in oxygen (20 Pa) and vacuum are given.In the submicronic powder ZnO (pure for analysis) of which targets are made, significant amount of perfect crystalline nanostructures (nanotetrapods, nanorods, etc., Figure2(a)) is revealed. Narrow, high intensity peaks on XRD pattern of submicronic powder (Figure 1(a)) also confirm its high crystallinity. In Figures 2(b)–2(d) it is visible that all NPs formed during electron evaporation had similar morphology and consisted of the agglomerated NPles with the shape close to spherical, up to 10–20 nm in size; thus agglomerates were of the nano- and submicronic sizes. Note the existence of significant amount of amorphous particles of an arbitrary shape (Figure 2(d)) and separate core-shell particles (inserts in Figure 2(b) and Figure 2(c)) in NPs.Figure 1
XRD pattern of (a) ZnO submicron powder, (b) ZnO nanopowder (Po
2 = 45 Pa), (c) NP ZnO-Zn, and (d) NP ZnO-Zn-Fe (x
F
e = 0.619 wt %).Figure 2
(a) SEM picture of particles of submicronic powder (target) ZnO (designation: T, nanotetrapods; R, nanorods); (b) TEM NP ZnO-Zn picture (on the insert, core-shell nanoparticle ZnO with amorphous shell); (c) TEM picture NP ZnO-Zn-Fe (on the insert, the electron diffraction pattern from the amorphous area of sample); (d) TEM picture of agglomerate nanoparticles ZnO-Zn-Fe (on the insert, the electron diffraction pattern from the crystalline area of sample).
(a)
(b)
(c)
(d)Quantitative EDX analysis from several local areas of sample ZnO-Zn-Fe (x
F
e
=
0.619 mass.%, ICP) showed considerable dispersion on concentration of Fe (from 0.17 up to 3 mass. Fe%) and lack of other impurity elements in sample. Results of EDX analysis from sample area (it is shown on Figure 3 insert) by ZnO-Zn-Fe are given in Figure 3. Red color shows spectral lines from the copper grid.Figure 3
EDX spectra of sample ZnO-Zn-Fe (x
F
e
=
0.619 mass.% (ICP)).Distribution of elements O, Fe, and Zn on several areas of the sample ZnO-Zn-Fe (Figure4(a)) is qualitatively estimated by means of EDX mapping by the STEM method (Figures 4(b)–4(d)). Mapping showed uniform distribution of atoms O and Zn. However, distribution of atoms Fe (Figure 4(d)) is less uniform. In Figure 4(d) the tendency to formation of curved “chains” atoms can be observed. Formations of visible congestions from atoms Fe (Fe clusters) are not observed. In Figure 4(e) there is EDX range of the sample ZnO-Zn-Fe where it is presented that the sample generally contains atoms Zn and O, with trace quantity (and trace) of the Fe element. On an insert of Figure 4(e) it is shown that the concentration of Fe in this sample was about 0.17 mass.%.Figure 4
(a) STEM image of ZnO-Zn-Fe sample; (b), (c), (d) the corresponding EDX mappings of O, Zn and Fe; (e) EDX spectra of sample ZnO-Zn-Fe.
(a)
(b)
(c)
(d)
(e)


## 3.2. Magnetic Properties and Phase Transformations of NPs

For the purpose of receiving NPs ZnO-Zn with the minimum content of parasitic impurity, we carried out powder deposition on a glass substrate. Target material from the submicronic powder ZnO previously was checked on Faraday’s scales. Results of measurements showed the existence of weak ferromagnetic response in submicron powder (1,5
∗
10
-
3 emu/g) connected, either with impurity or with presence at powder quantity of perfect nanostructures (nanotetrapods and nanorods, Figure 2(a), are shown by shooters) which, as we know, possess their own RTFM [35, 41, 43].The increased magnetization of NP ZnO-Zn besieged on metal substrates most likely was caused by the impurity formed in powders owing to the reverse diffusion of substrates elements at high-temperature deposition.Curves of magnetization (M) are given in Figure 5 at the room temperature for NP ZnO-Zn (34 mass.% Zn) from a glass substrate in a magnetic field 12 kOe.Figure 5
Room temperatureM
-
H curves for ZnO-Zn NP: (1) as prepared and (2) after annealing.NP ZnO-Zn showed a weak ferromagnetic response at room temperature, equal to7
∗
10
-
3 emu/g.The growth of magnetization of sample ZnO-Zn after short-term annealing in the air atmosphere (temperature of annealing of 300°C, time of annealing of 30 min.) appeared to be unexpected; magnetization of the annealed sample grew to 9,5
∗
10
-
3 emu/g.Note that the growth of magnetization NPles of pure ZnO after annealing in the oxidizing atmosphere is observed in work [65]; the growth of magnetization is explained with formation of clusters from oxygen vacancies. In our case, it is the most probable that the growth of magnetization was caused by a process of phase transformation (oxidation) of NPles Zn in ZnO oxide when annealing. Considering the small duration and low temperature of annealing, we do not exclude that the process of oxidation Zn to ZnO took place not completely that could lead to formation of some quantity of core-shell structures of ZnO-Zn (a diamagnetic core from Zn and a shell from amorphous ZnO). The example such of a core-shell structure in NP ZnO-Zn is shown on Figure 2(b) insert. It is probable that the process of oxidation of NPles Zn and forming of core-shell structures leads to increase of the concentration of oxygen vacancies in the annealed sample that was reflected in magnetization growth.Note the increase of diamagnetic contribution to the specific magnetization of sample ZnO-Zn in magnetic field higher than 7 kОe. Thus, strengthening of magnetization NP ZnO-Zn after annealing can be caused by a number of factors: formation of amorphous layers on borders between ZnO nanoparticles, generation of core-shell structures with the broken stoichiometry on the interface between core and shell, and clustering of oxygen vacancies.In particular, emergence of ferromagnetic properties in films of pure ZnO at the expense of formation of foam-like grid from amorphous ZnO between NPles is shown in Straumal’s numerous works [11] and correlates with our data.Besides, the number of experimental works accruing every year much more confirms that carriers of a charge are not so necessary for RTFM emergence; in particular, ferromagnetic interaction is observed in films without free carriers in a dielectric condition [10, 66–71]. In our case, after annealing of conducting NP ZnO-Zn as a result of oxidation of NPles Zn the number of free carriers sharply decreased (powder turned into dielectric) that directly correlates with conclusions [10, 66–71]. The growth of magnetization of NP ZnO-Zn after annealing proves that the role of free carriers in RTFM formation in annealed NP ZnO-Zn is insignificant. Note works [72, 73] where the inverse correlation between magnetization and electronic density was shown.In Figure6 magnetization curves are given at the room temperature of NP ZnO-Zn-Fe (x
F
e
=
0.128, 0.569, 0.619 mass.%) in a magnetic field 12 kOe [59].Figure 6
Magnetization change at room temperature in NP ZnO-Zn-Fe in relation to concentration of Fe.From Figure6 it follows that dependence of the magnetic moment on atom of Fe (μ
B/Fe) from x
F
e in NP ZnO-Zn-Fe is nonlinear. The maximum magnetic moment (0,272 μ
В/Fe) is determined in NPs at an intermediate concentration of x
F
e
=
0,569 mass.% that confirms, noted above, lack of direct correlation between magnetization and concentration of iron magnetic ions in powders and will be coordinated with conclusions [10–13, 71].In particular, authors of the work [11] connect ferromagnetism of ZnO not with entered ions of transitional metals but with the magnetic moments in vacancies of lattice which concentrate on borders of grains. Therefore, the introduction of ions Fe probably only promotes emergence (strengthening) of ferromagnetism in NP ZnO-Zn-Fe due to emergence of noncoupled spins Fe2+(Fe3+) ions and to increase in disorder and defectiveness of NP structure at doping (that confirms corresponding change of ZnO-Zn-Fe lattice parameters).Further increase in concentration of Fe in NP ZnO-Zn-Fe with 0,569 up to 0,619 mass.% led to decrease in magnetic response. Decrease in magnetization shows that magnetization of NP is not connected with possible formation of secondary phases and type of clusters Fe, Fe3O4, or γ-Fe2O3. If pure Fe or its oxides were responsible for ferromagnetic behavior of NP, the increase in concentration of x
F
e in samples would lead to an increase in a volume fraction of these phases in samples and the related magnetic response.Magnetization curves of samples withx
F
e
=
0,569 and 0,619 mass.% did not reach saturation in the magnetic field to 12 kOe. That points at strengthening of paramagnetic contribution to magnetization. Strengthening of antiferromagnetic interaction between the neighboring Fe-Fe ions suppresses ferromagnetism at high concentration of Fe. In particular, the similar behavior was traced in ZnO-Fe NPles in [74], where with x
F
e growth up to 20 at.% the increase of paramagnetic contributionoccurred. Note that, in [74] with the comparable sizes of particles, our NPles had magnetization of nanoparticles 10 times less which can be explained by smaller concentration of the defects formed during the chemical method.It is known [75] that creation of effective exchange interaction between magnetic ions in DMS requires rather high concentrations of dopant (usually units%), with rare exception [10, 76]. In our NPs concentrations of magnetic dopant were 10 times less than the threshold that directly specifies that the mechanism of observed ferromagnetism is not defined by short-range exchange interaction between magnetic ions of dopant, improbable because of long distances between ions, and is more connected with defects of various types which were formed in NPles as a result of nonequilibrium crystallization of NPles with high temperature on cold glass substrates.In addition, the question of the ferromagnetism nature in heterophase NP ZnO-Zn-Fe complicates the existence of amorphous components in NP detected from XRD and the microscopic analysis. Influence of dimensional factor on magnetization of NPs from the fine-crystalline phases ZnO and Zn is not excluded.After annealing of the conductive ZnO-Zn-Fe nanopowder, as a result of the oxidation of Zn nanoparticles the powder transformed into a dielectric. In such NPs density of electric carriers is low that excludes a possible explanation of ferromagnetism in NPs ZnO-Fe using the carrier-mediated exchange mechanism.In Figure7 magnetization curves of NPs ZnO-Fe (x
F
e
=
0.128, 0.569, 0.619 mass.%), received on the vibration magnetometer in magnetic fields ±1 T are given at the room temperature. Note the considerable strengthening of samples ZnO-Fe magnetization in comparison with magnetization of nonannealed NPs ZnO-Zn-Fe. Magnetization of samples with concentration of x
F
e
=
0.128, 0.569, 0.619 mass.% grew by ≈ 5, 2.5, and 2 times, respectively. Strengthening of magnetization of undoped sample ZnO-Zn after annealing (Figure 4) was much less (35%) that is possible to explain with non-full oxidation of NPles Zn to ZnO at lower temperature of annealing (300°C) and small time of annealing (30 min.).Figure 7
M versus H curves for ZnO-Zn-Fe NPs with various doping concentrations.Note that the magnetization of our samples is 10 times more than magnetization of samples ZnO-Fe with close concentration of dopant (≤1%) received with use of traditional ceramic synthesis (x
F
e of = 1%, M
S = 1,25
∗
10
-
2 emu/g, [42]), method sol-gel [28]) that obviously points to a defining role of structural defects on strengthening of ferromagnetic response and preference of use of strongly nonequilibrium methods for formation of structural defects in various materials, before methods of wet chemistry.The general nature of magnetization change of samples ZnO-Fe from a concentration of Fe remained the same, as with nonannealed samples of ZnO-Zn-Fe. All samples of ZnO-Fe showed RTFM and had well-defined hysteresis with coercive force in the range from 160 to 380 Oe. Thus, the sample withx
F
e
=
0.128% was completely saturated in the magnetic field ±1 T though curves magnetizing is exemplary with x
F
e
=
0.569 and 0.619 continued to grow with increase in the magnetic field and did not come for saturation. Similar change of magnetization curves with growth of a dopant concentration quite often has been observed in ZnO-Fe system before [28, 77, 78]. Note that the hysteresis loop measured on the ZnO-Fe sample (0.128%) is thinner than those measured on the other samples.The broadening of hysteresis loops is caused by the fact that with the growth of dopant concentration the average distance between ions of Fe decreases (see Table2) and antiferromagnetic exchange energy of ions Fe becomes less than ferromagnetic exchange energy; therefore the magnetic moments of ions Fe are ordered antiferromagnetically that reduces magnetism of samples [79].Now, in the theory of ferromagnetism DSM two models [10] connected with a charge transfer and with the formation of the connected magnetic polarons dominate.The ferromagnetism nature in NPs ZnO-Fe received can be explained using the model of the connected magnetic polarons [80].Polarons are in a low-doped sample (0.128% of Fe) at rather long distances from each other to carry out strong exchange interaction. Apparently, in a sample with a concentration of dopant of equal 0.519 mass.%, the distance between the neighboring polarons decreases and becomes optimum; therefore, the exchange between two neighboring magnetic polarons amplifies. It is possible that in a more strongly doped sample (x
F
e
=
0.619) the magnetic moment quickly decreased due to strengthening of dopant-dopant associations that brought progressive reduction of the orbital moment. Reduction of the magnetic moment in NPs ZnO-Fe with the growth of concentration Fe also indirectly confirms lack of the secondary magnetic phases Fe in the sample and is consistent with the XRD data. Consider the following:(A)
Similar picture of magnetization strengthening samples after annealing as in NPs ZnO-Zn and ZnO-Zn-Fe, observed earlier in ZnO-Zn-Cu system (300°C, time of annealing of 30 minutes) [81].
(B)
Magnetization growth in undoped Fe NPs ZnO-Zn and ZnO-Zn-Cu (the content of Fe impurity in the above samples according to ICP of the analysis did not exceed10
-
3
–
10
-
2 mass. Fe % that is 1-2 orders less than concentration of ions Fe in NPs ZnO-Fe (ZnO-Zn-Fe) directly specifies that the ferromagnetic response is not connected with magnetic ions Fe.
(C)
It is the most probable that, when annealing NPs ZnO-Zn and ZnO-Zn-Cu as the result of NPles Zn oxidation to NPles ZnO, recrystallization of NPles, partial crystallization of amorphous fraction, generation of core-shell structures (the core-Zn, the shall-ZnO), the concentration of various structural defects (oxygen vacancies, cation vacancies, interstitial atoms, dislocation, etc.) in NPs changed in a complex manner, which led to strengthening of magnetization samples.Dynamic heating of sample ZnO-Zn-Fe in the air atmosphere using the DSC-TG method also showed (Figure 8(b), curve TG) that full oxidation of nanoparticles Zn comes to the end at temperature ≈ 600°C that in addition confirms the possibility of preservation of core-shell structures in powder at short-term annealing at the temperature of 500°C.Figure 8
Heating thermograms DSC-TG and the mass spectra H2O and CO2 of the NPs ZnO-Zn (a) and ZnO-Zn-Fe (b).
(a)
(b)Oxidation of NPles Zn in NP ZnO-Zn-Fe began from temperature ≈ 200°C (exothermic peak 1 at curve TG in Figure8(b)) which is slightly higher than the temperature of the oxidation beginning NP ZnO-Zn equal to 110°C (Figure 8(a), curve TG). Thus, Fe introduction in ZnO inhibits temperature of the oxidation beginning of NPles Zn and reduces the speed of oxidation reaction NPles Zn in doped powder. Oxidation of NPles Zn comes to the end in NP ZnO-Zn (curve TG, Figure 8(a)) and ZnO-Zn-Fe (curve TG, Figure 8(b)) at temperatures of ≈280°C and 600°C, respectively.In our opinion, the new model of ferromagnetism is the most suitable one for an explanation of the nature of RTFM in systems ZnO-Zn and ZnO-Zn-Fe (Cu) in the diluted magnetic oxides (charge-transfer ferromagnetism model), offered by Coey et al. [82] which is based on the Stoner type of ferromagnetism connected with electrons in percolation defective structures, such as the grain boundaries.This model has successfully been applied to an explanation of ferromagnetic interaction in NPles of semiconductor oxides and doped ions of transitional metals in the mixed valent state [10, 83]. In particular, charge-transfer ferromagnetism model has been used for RTFM explanation in objects films of Z
n
x
Z
n
O
1
-
x close to our NP [84] and core-shell Zn/ZnO [85] structures. Besides the model does not assume homogeneous distribution of magnetic dopant on the sample that in the best way approaches the situation (Figure 4(c)).Thus, we showed that magnetism of low-doped (x
F
e
≤
0,619 wt.%) and undoped Fe NPs on the basis of ZnO is their intrinsic property. The dominating contribution to ferromagnetism of samples is made by various structural defects (oxygen vacancies, interstitial atoms of introduction, and amorphous component), instead of charge carriers.It is determined that there is nonlinear dependence of magnetization on concentration of magnetic dopant in NP ZnO-Zn-Fe and ZnO-Fe. The maximum magnetic moment in samples of ZnO-Zn-Fe and ZnO-Fe is observed at concentration of magnetic dopant equal to 0,519 wt.% which is much lower than a percolation threshold.The received results will be coordinated with Pan et al. [10] given the review where it is shown that the maximum magnetic moment in ZnO-Fe systems (Cu, Cr, Ni) is usually observed at concentration of dopant ≈ 1 аt.%. However, further work on ferromagnetism studying of the zinc oxide alloyed by Fe is required. It will be oriented to the establishment of an unambiguous correlation between defectiveness of structure and magnetic properties and the identification of defects in their nature and the mechanism of their interaction leading to the emergence of ferromagnetism at the room temperature.


## 4. Conclusions

With the help of evaporation the pulsed electron beam in vacuum and oxygen NPs ZnO, ZnO-Zn, and ZnO-Zn–Fe was received. The specific surface area of samples did not exceed 45 m2/g. The bimodal distribution of the phase ZnO with wurtzite structure on fractions and existence of amorphous components in all NPs without any exception is shown. All powders possessing similar morphology are agglomerated (in agglomerates of the nano and submicronic sizes) and have the shape of particles close to spherical being not over 20 nm in size. The data of electronic microscopy confirm the existence of core-shell structures with a metal core Zn and an amorphous oxidic shell in powders. The concentration of Fe in samples was less than 0,619 wt.% that is much lower than the percolation threshold. By means of mapping rather uniform distribution of Fe in ZnO lattice was established.Doped and undoped iron NPs on the basis of ZnO showed RTFM which considerably (4-fold growth at the sample with the minimum concentration of dopant) increased after NP annealing in the air. The growth of magnetization is caused by phase transformation (oxidation of nanoparticles Zn to ZnO) and formation of additional structural defects (generally oxygen vacancies) when annealing.The inhibiting influence of a doped Fe on temperature of the beginning of nanoparticles of Zn oxidation and decrease in speed of oxidation reaction in nanoparticles Zn in doped powder in comparison with NP ZnO-Zn are established.The lack of logical correlation between the magnetic moment and concentration of dopant iron in NP ZnO-Zn-Fe and ZnO-Fe is shown. The mechanism of RTFM emergence in the samples containing metal particles of Zn can be explained by means of the charge-transfer ferromagnetism model in the diluted magnetic oxides. For RTFM explanation in the annealed samples of ZnO-Fe with a lowered density of electric carriers the model of the connected magnetic polarons is more suitable.



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