Journal of Nanotechnology
Volume 2015 (2015), Article ID 417817, 8 pages
http://dx.doi.org/10.1155/2015/417817

Research Article

Properties of Silicon Dioxide Amorphous Nanopowder Produced by Pulsed Electron Beam Evaporation

Vladislav G. Il’ves,1,2 Michael G. Zuev,2,3 and Sergey Yu. Sokovnin1,2

¹Institute of Electrophysics, Ural Branch of the Russian Academy of Sciences (RAS), Amundsen 106, Yekaterinburg 620016, Russia
²Ural Federal University Named after the First President of Russia B. N. Yeltsin, Mira 19, Yekaterinburg 620002, Russia
³Institute of Solid State Chemistry, Ural Branch of RAS, Pervomayskaya 101, Yekaterinburg 620049, Russia

Received 24 July 2015; Revised 21 September 2015; Accepted 29 September 2015

Academic Editor: Carlos R. Cabrera

Copyright © 2015 Vladislav G. Il’ves 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.

Abstract.

SiO₂ amorphous nanopowder (NP) is produced with the specific surface area of 154 m²/g by means of evaporation by a pulsed electron beam aimed at Aerosil 90 pyrogenic amorphous NP (90 m²/g) as a target. SiO₂ NP nanoparticles showed improved magnetic, thermal, and optical properties in comparison to Aerosil 90 NP. Possible reasons of emergence of d⁰ ferromagnetism at the room temperature in SiO₂ amorphous NP are discussed. Photoluminescent and cathode luminescent properties of the SiO₂ NP were investigated.

1. Introduction

Messages that silicon [1, 2] and silicon dioxide (SiO₂) [3, 4] possess noticeable magnetic properties at room temperature appear now in increasing frequency. Besides, porous silicon is widely known for the bright white luminescence [5, 6], and amorphous nanostructures (nanowires, nanoedges, nanotubes, etc.) from silicon dioxide emit intensive blue light [7, 8]. Researches of magnetic and luminescent properties at Si/SiO₂ [9–13] interface are actively conducted.

In particular, an actual task is the creation of a luminescent light source on the basis of one material in which luminescence spectra contain bands where total radiation gives white luminescence [14].

Inexpensive, with small content of chemical impurities, SiO₂ pyrogenic nanopowders (NPs) (commercial name: Aerosil, by Degussa company) are convenient for production of an evaporated target in gas-phase methods for producing powders (laser ablation, thermal evaporation, magnetron sputtering, etc.), in particular, at pulsed electron beam evaporation [15].

Magnetic and optical properties of silicon and its compounds indicate possibility of simultaneous production of new modified magnetic-luminescent materials on the basis of Si-SiO₂ system in powder or thin film form, in amorphous, crystalline, or mixed amorphous-nanocrystalline states with improved parameters. Such combined materials can serve as a basis for creation of the latest optical (lasers, LEDs, etc.) and spintronic devices [16, 17].

The purpose of this work consisted in producing SiO₂ nanopowder by target evaporation from Aerosil 90 NP in vacuum by means of the pulsed electron beam and investigation of main properties of the nanopowder produced.

2. Experimental

SiO₂ amorphous nanopowder has been produced on NANOBIM-2 [15] installation by pulsed electron evaporation in vacuum (residual pressure: 4 Pa). NP was deposited on large-surface glass noncooled substrates located around the target at the distance of 10–15 cm.

The target was made of Aerosil 90 NP [18] which was preannealed for 2 hours at temperature of 1100°C to improve pressing of the target from the annealed powder by means of manual press.

Mode of the target evaporation was as follows: accelerating voltage: 37 kV, beam current: 0.5 A, pulse duration: 100 μs, pulse repetition rate: 100 Hz, target rotation speed: 2.5 turns/min, and evaporation time: 20 min. NP collection from glasses was 0.3 g. Produced NP differed from the friable and fluffy Aerosil powder considerably. Upon removal from the glass surface by means of titanic foil, the powder coagulated in rolls, while certain portions of the coating were rolling down in rolls spontaneously in the course of deposition. NP appearance indicated its fibrous texture.

The following diagnostics were used for analysis of NP properties: powder X-ray diffraction (XRD) was made on XRD 7000 diffractometer; the powder specific surface area () was defined by Brunauer-Emmett-Teller (BET) method on Micromeritics TriStar 3000 installation; magnetic characteristics were defined on Cryogenic CFS-9T-CVTI vibration magnetometer at 300 K. Thermograms of heating/cooling and mass spectrums were recorded by means of differential scanning calorimetry (DSC) and thermogravimetric (TG) measurements methods on STA-409-PC Luxx synchronous thermoanalyzer combined with QMS-403C mass spectrometer by NETZSCH, in the temperature range 40–1400°C.

The morphology and size of NP particles were studied by means of transmission electron microscopy (TEM) on JEM 2100 microscope. Concentration of impurity iron in SiO₂ was determined by methods of energy-dispersive X-ray (EDX) spectroscopy on TEM and mass spectrometry with inductively coupled plasma (ICP) on ELAN 9000 spectrometer. Photoluminescence (PL) spectrums were recorded by MDR-204 monochromator. Infrared (IR) absorption spectrums were recorded by Spectrum one device by Perkin-Elmer from powders suspended in vaseline oil in the frequency range from 400 to 1000 cm⁻¹. The pulsed cathodoluminescence (PCL) was investigated with KLAVI_1 setup.

3. Results and Discussion

According to BET analysis, of SiO₂ NP was 154 m²/g ( of Aerosil NP is equal to 90 m²/g, according to the producer’s data [18]).

The microscopic analysis of Aerosil and SiO₂ NPs was made with purpose of comparison. TEM pictures of studied NPs are given in Figure 1; the illustration allows seeing well the distinction in porosity and sintering behaviour of the compared powders. Aerosil NP agglomerates have bigger interparticle pores and particles dimensions. The form of Aerosil particles (Figure 1(a)) is close to spherical; the surface of particles is smooth and does not contain pores. Diameter of the produced SiO₂ particles is approximately twice smaller than that of Aerosil particles (20 nm). The form of the produced SiO₂ particles is far from spherical (Figure 1(b)), and the surface of particles is rough.

(a)

(b)

(c)

(d)

Figure 1: (a, b) TEM pictures of Aerosil 90 NP and (c, d) of SiO₂ NP, produced with various magnifications. On the insert of (d), see the electron diffraction pattern from the amorphous area of the sample.

Particles of SiO₂ NP (Figure 1(d)) are sintered much stronger than particles of Aerosil (Figure 1(b)). It is an important factor that indicates emergence of ferromagnetic properties (d⁰ ferromagnetism [20]) in pure diamagnetics and SiO₂ in particular.

The data of the X-ray phase analysis (Figure 2) and the electron diffraction analysis (insert in Figure 1(d)) confirmed the amorphous condition of SiO₂ NP and absence of secondary magnetic phases therein in the form of pure iron and its oxides.

Figure 2: XRD patterns of SiO₂ NP before and after annealing at temperature of 1000°C within 24 hours. Peaks designated by arrows: 1, quartz; 2, cristobalite; 3, crystalline structure of SiO₂ [19].

The XRD patterns of SiO₂ NP before and after annealing sample at temperature of 1000°C in the air atmosphere are shown in Figure 2.

The sample before annealing is completely amorphous (no Bragg peaks). In the annealed sample, the crystalline phases of SiO₂ of three structural modifications are found: quartz (PDF 00-046-1045), cristobalite (PDF 00-039-1425), and crystalline structure of SiO₂, prepared by the sol-gel method (PDF 01-075-3159, [19]). The crystallinity degree of the annealed sample, as calculated in the XRD Crystallinity program, was 17%.

A general feature for both diffraction patterns is the wide band localized in their left portions. However, the top of the band is shifted after annealing (-shift of the band top) to lower values of diffraction angles, from 24 to almost 22 degrees (Figure 2). It is worth noting that cristobalite possesses the main peak of diffraction at ≈22°, and many authors noted correlation of the wide band shift , induced by heat treatment, with structural conformational changes in the silica grid [19].

By means of thermal analysis, it is established that, at dynamic heating of samples with the speed of 100°C/min, the produced SiO₂ NP starts to crystallize at temperature about 1050°C (see endothermic peak in Figure 4(a)) and stops crystallizing at temperature about 1280°C. Please note that on Aerosil thermogram (Figure 3(b)) the corresponding exothermic peak from crystallization of the amorphous phase is hardly noticeable.

(a)

(b)

Figure 3: Heating curves of DSC-TG and H₂O mass spectrums in the temperature interval of 40–1400°C: (a) amorphous SiO2 NP and (b) amorphous Aerosil 90 NP.

(a)

(b)

Figure 4: (a) Field dependent magnetization of Aerosil 90 NP in magnetic field ±7 T. (b) Anhysteretic magnetization curve of undoped SiO2 NP in magnetic field ±7 Т.

Partial crystallization of Aerosil NP amorphous phase at dynamic heating is indicated by the insignificant deviation of the baseline of DSС curve at temperature about 1250°C (Figure 3(b)), whereas all parameters of the exothermic peak (temperature of beginning/completion of amorphous phase crystallization, the exothermic peak maximum) are displaced towards high temperatures approximately by 200°C, in comparison with the corresponding parameters of the produced SiO₂ NP.

Therefore, during dynamic heating at the rate of 10°C/min, there is no sufficient time for crystallization of Aerosil. The reason of distinction in temperatures of crystallization beginning in the amorphous powders under study is related to their morphology. As it was noted above, the produced particles of SiO₂ possess more developed rough surface (Figure 1(c)), in comparison to the smooth surface of Aerosil’s spherical particles (Figure 1(a)), which contributes to the decrease of their crystallization temperature in the amorphous phase and, respectively, of sintering temperature. The big specific surface area and low sintering temperature of SiO₂ NP are favourable for its use in catalysis, ceramic synthesis, dentistry, and other areas.

Weight decrease during SiO₂ NP heating up to 800°C (9.25 wt.%) exceeds the respective loss of mass of Aerosil NP almost twice (see TG and water mass spectrums curves in Figures 3(a) and 3(b)), which indicates the increased hydrophility of the produced NP.

According to magnetic measurements, it is established that Aerosil NP shows typical diamagnetic behavior (Figure 4(a)), while SiO₂ NP shows ferromagnetic behavior at room temperature (Figure 4(b)). The magnetization curve of SiO₂ NP is anhysteretic, which is characteristic for d⁰ ferromagnetics, both pure and doped with nonmagnetic elements [20, 21]. The saturation magnetization of SiO₂ NP was 0.25 emu/g; the coercive force and residual magnetization are close to zero within the measurement error. Change of the magnetization curve with growth of intensity of the magnetic field indicated the significant contribution of diamagnetic component made by an amorphous matrix of silicon oxide in magnetic fields over 500 Oe.

The chemical analysis of NP SiO₂ made by the ICP and EDX methods showed that concentration of impurity iron does not exceed (7.4) 10⁻² and (1–3) 10⁻² wt.%, respectively.

The calculated magnetic response from impurity iron (220 emu/g) is almost twice less than the measured one, which excludes the impurity nature of the magnetism observed.

The aforesaid is confirmed by results of work [22] where the maximum magnetization of saturation nanocomposite films Fe₂O₃/SiO₂ was 10 times less (2.125 10⁻² emu/g) at concentration of Fe₂O₃ (30% wt.) 300 times higher than in our sample SiO₂.

Specified in Figure 5 are IR spectra of amorphous Aerosil silicon oxides and produced SiO₂ NP. A sample of SiO₂ NP demonstrated the shift of frequencies in the smaller values area (Table 1). This shift could indicate some extent reduction of polymerization of silicon and disordering of its amorphous structure in the course of SiO₂ evaporation [23]. Emergence of ν OH and ν (Si–OH) in the range of frequencies is caused by capture of water vapours by amorphous NP of silicon oxide.

Table 1: Frequencies (cm⁻¹) in the infrared spectra of silica.

Aerosil 90
SiO₂ NP
Assignment

472
465
ν ₂ SiO₄

810.5
803
ν(Si–O–Si)

—
885
ν OH

—
941
ν(Si–OH)

Figure 5: IR spectra of silicon oxides (1: Aerosil, 2: SiO2 NP).

Room temperature PCL spectra of SiO₂ NP are shown in Figure 6. The spectra overlap practically all visible range of waves lengths. Values of the peaks centers are presented in Table 2 in the range obtained at Gaussian decomposition of bands by means of the program ORIGIN.

Table 2: The centers of the peaks in the spectrum of pulsed cathodoluminescence NP SiO₂ (Figure 6).

Peak, number
Peak centres
Association
References

nm
eV

1
451.5
2.74
Twofold coordinated silicon centers ≡Si–Si≡
[30]

Oxygen-deficient centers
[30, 42]

2
513
2.4
Self-trapped exciton
[34]

Oxygen vacancy related defect
[24]

3
590
2.1
Nonbridging oxygen hole centers (NBOHC) ≡Si–O•
[43]

Hydrogen-related defects (the OH group)
[24]

4
618
2.00
Fe³⁺ (transition (4G) → (6S))
[31]

Si nanocluster
[25, 35]

The nonbridging oxygen hole centers (NBOHC) ≡Si–O•
[37, 39]

The quantum confinement effect
[38, 39]

Defects in the Si oxide/Si interface
[26, 39–41]

5
649
1.91
Nonbridging oxygen hole centers (NBOHC) ≡Si–O•
[24]

6
683
1.81
≡Si–O–O•
[43]

Si nanocluster
[24, 25, 36]

7
702
1.76
Si nanocluster
[24, 25, 30, 36]

8
743
1.67
Si nanocluster
[24, 25, 30, 36]

9
795
1.56
Si nanocluster
[25, 36]

Figure 6: Deconvolution into Gaussian components of the PCL spectra of SiO2 NP.

Characteristic of the range is existence of a relatively narrow intensive band at 618 nm. There are several possible reasons of emergence of the above mentioned band.

The cathodoluminescence spectra in Figure 6 consist of 9 partially overlapping bands: (i) one band in the blue region at about 451.5 nm arising from oxygen deficiency-related centers (ODC) or twofold-coordinated silicon centers (≡Si–S≡), which are generated in the presence of oxygen vacancy sites; (ii) one band in the green region at around 513 nm which can be connected with deficiency of oxygen (oxygen vacancies), or the autolocalized excitons (self-trapped exciton); (iii) one yellow band at about 590 nm connected with the hole centers on the nonbridging oxygen atoms (nonbridging oxygen hole center—NBOHC) and with the presence of the OH group; (iv) and series from 6 red bands in the energy range 1.56–2.0 eV, mostly connected with silicon nanoclusters.

Rather weak band with a maximum at 1.91 eV (number 5 in Figure 6) with a high probability is connected with the radiation of nonbridging oxygen atom which is considered one of the most well studied point defects in glass [24].

The luminescence of the other four red bands (numbers 6–9 in Figure 6) is most possibly connected with existence of silicon nanoclusters in the received SiO₂ NP [25].

Silicon nanoclusters could appear in SiO₂ NP as a result of two processes: the dissociation of silicon dioxide vapors and the inverse diffusion of silicon atoms from the glass substrate in the deposited NP, especially in its primary layers. In Zamoryanskaya’s works [24, 26–29], it is shown that direct impact of an electron beam on silicon dioxide leads to formation of silicon nanoclusters in it. However, in this method of receiving nanoparticles, direct influence of primary electrons after NP deposition on a substrate is excluded; however, they can form by target evaporation. Nevertheless, characteristic bands of luminescence from silicon nanoclusters in the energy range from 1.4 to 1.8 eV [25] are present in the range of Figure 6. Four peaks on cathodoluminescence spectra (numbers 6–9) in the energy range from 1.56 to 1.81 eV confirm existence of Si nanoclusters in the received NP.

Peak number 7 has the largest area. Correlation of silicon nanoclusters average diameter and the energy of photoluminescent peak [30] shows that the 1.76 eV energy matches silicon nanoclusters with the diameter of 4 nm. On TEM picture (Figure 1(d)), the separate and sintered SiO₂ nanoparticles with the diameter from 4 to 5 nm and less are well visible (shown by arrow) which confirms communication of the cathodoluminescent peaks numbers 6–9 with silicon nanoclusters of small size, less than 5 nm.

Extensive amorphous halo and lack of concentric rings on the diffraction pattern of a sample (insert in Figure 1(d)) confirm that silicon nanoparticles and SiO₂ in the received SiO₂ NP were in an amorphous state.

The main feature of cathodoluminescence spectra is existence of a narrow intensive band at 618 nm (peak number 4 in Figure 6). We will give the possible causes for emergence of this band. Here are the possible causes of this band:

(1)At the sample of SiO₂ NP, there is an insignificant impurity of Fe ions (1–7.4) 10⁻² wt.%. Therefore, the band at 618 nm can allegedly be carried to the luminescence Fe³⁺ ions (transition 4G → 6S [31]). In [32], in minerals, the luminescence band from Fe³⁺ ions usually located in the range from 640 to 820 nm with maximum 730 nm (e.g., in quartz).(2)From the evolution of the cathodoluminescence spectrum of pure silica, it is known [30] that the relative intensity of the red band significantly increases and its full width at half-maximum (fwhm) decreases with increasing acceleration voltage; thus, tops of red and blue bands peaks seek to separate from each other with growth energy of electrons (energy of electrons in the KLAVI 1 installation (180 keV) is 10 times bigger than that of electrons (15 keV) from [30]). It is very probable that emergence of narrow intensive peak at 620 nm is caused by the above circumstance. The feature of cathodoluminescence range of silicon glass [30] reduction of ultraviolet band intensity (up to the total disappearance) during increase of accelerating voltage is confirmed by lack of peak in UV band (Figure 6).(3)Emergence of a band at 618 nm can be connected with the presence of nanodimensional silicon at the received powder.

In the literature, the nature of a spectral band in the energy range from 2.0 to 2.2 eV is explained even more widely. Luminescence at 620 nm in amorphous SiO₂ is connected with the trivalent silicon center [33], self-trapped exciton [34], silicon nanoclusters [35, 36], the nonbridging oxygen hole center (NBOHC) [37], quantum confinement effect [38], defects on the Si/SiO₂ [39–41] interface, and so forth. Considering relatively difficult cathodoluminescence spectra given in the real work for unambiguous interpretation of the luminescence centers in the received NP SiO₂, further researches with attraction of additional spectral methods are necessary.

Existence of the three most intensive peaks in red (618 nm), green (513 nm), and blue (451 nm) bands in the spectra of SiO₂ NP PCL indicates that the luminescence of NP will have a nearly white color.

4. Conclusions

Thus, by means of evaporation by the pulsed electron beam, an amorphous magnetic and luminescent SiO₂ NP is produced which has the following features:

(1)The powder consists of amorphous particles less than 10 nm in size, the form of particles is far from spherical, and the surface of particles is rough. Only Aerosil 380 NP with a high specific surface (380 m²/g) has similar particles, of a wrong form and size near about 7 nm [18].(2)The powder belongs to soft magnetics and possesses anhysteretic magnetization curve [20, 21] which is peculiar for d⁰ magnetics; saturation magnetization reaches 0.25 emu/g; coercive force and residual magnetization are close to zero.(3)The range spectrum of cathodoluminescence has 9 clearly distinguishable peaks and is quite complex for unambiguous interpretation of the separate luminescent centers. Emergence of a narrow, intensive band at 618 nm can be connected with formation of silicon nanoclusters or with the presence of impurity iron ions or with dependence of intensity of cathodoluminescence on the size of electron beam energy in the KLAVI 1 spectral analyzer.(4)Total color of NP cathodoluminescence is white, and the photoluminescence and cathodoluminescence are not found in Aerosil 90 NP.

Highlight

The amorphous nanopowder SiO₂ with a specific surface 154 m²/g was received by means of evaporation of a target pressed from commercial nanopowder Aerosil 90.

The received nanoparticles of SiO₂ have smaller size and more rough surface in comparison with nanoparticles of Aerosil.

The comparative analysis of magnetic, thermal, and optical properties of both nanopowders is carried out.

The undoped SiO₂ nanopowder showed ferromagnetic behavior at room temperature.

The nanopowder SiO₂ possesses white cathodoluminescence.

Conflict of Interests

The authors declare that there is no conflict of interests regarding the publication of this paper.

Acknowledgments

The research is performed with partial support of the projects of the Russian Foundation for Basic Research (nos. 15-08-01381, 12-03-31593-мол-а, and 13-03-00119-а) and Presidium Ural Branch of the Russian Academy of Sciences and Sverdlovsk Oblast Government (nos. 13-08-96056 P_URAL_а, 12-M-23-2007, and 12-T-З-1009) and Grant ERA.Net RUS Plus-S&T (NanoRadDos).

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