In-situ reactive synthesis of full dense Si2N2O by incorporating of Amourphous nanosized Si3N4;effect of MgO and Y2O3

Document Type : Research Paper


1 Department of Materials Engineering, Isfahan University of Technology (IUT), Isfahan, Iran

2 Materials Science and Engineering Department, University of Wisconsin- Madison, USA

3 Department of Materials Engineering, Malek Ashtar University of Technology, Shahin-Shahr, Iran


Si2N2O is considered as a new great potential structural/functional candidate in place of Si3N4. The amorphous Si3N4 nanopowder was incorporated into silica sol by adding of MgO and Y2O3 as sintering aid. Synthesized powders were heated by spark plasma sintering at a heating rate of 100 oC/min yielded fully dense compacts at 1550 and 1750 oC for 40 min. The phase formation of samples was characterized by X-ray diffraction technique and Raman spectroscopy. The microstructure was studied by field emission scanning electron microscopy equipped by energy dispersive X-ray spectroscopy. Optical emissivity of Si2N2O phase was investigated by photoluminescence spectroscopy. The obtained results confirm that employing MgO in compare to the Y2O3 could promote the fabrication of a fully dense pure Si2N2O specimen by SPS at much shorter time than conventional sintering. Si2N2O have a strong, stable blue emission band centered at 455 nm with excitation wavelengths of 240 nm .



Compounds in the Si–O–N system exhibit excellent thermal, chemical, and mechanical stability, as well as high diffusion barrier and good dielectric properties [1]. Silicon oxynitride (Si2N2O) is a unique compound in the Si3N4–SiOsystem and reflects an excellent oxidation resistance at severe conditions for high temperature structural purposes [2–4].

In addition, it possesses very low theoretic density (2.81 g/cm3), high hardness (HV: 17–22 GPa), low thermal expansion coefficient (3.5×10−6 K−1), good thermal shock resistance and high thermodynamic stability temperature (about 1800 C) [5–8]. Recently, based on ab initio calculations, Goumri-Said et al. [9] predicted that Si2N2O possessed low dielectric constant. However, there are not enough experimental results to evaluate this conclusion mainly because of difficulty of the bulk Si2N2O synthesis.

The reaction sintering process of Si2N2O is close to the sintering of Si3N4, i.e. both materials have strongly covalent bonds and low diffusion coefficient, requiring high sintering temperatures. This usually implies that oxide additives are needed to form a liquid phase with a eutectic melting point low enough to permit sintering without excessive dissociation [10]. Pressureless sintering (PLS) lead to formation of Si2N2O phase with purity of 80% by using equimolar mixture of SiO2 and Si3N4 with appropriate additives after heating in a long time under N2 atmosphere, in the best of circumstances [11]. Tong et al. [12] could synthesize the near theoretical density Si2N2O samples with purity of 98% at low temperature (1550 °C) by hot pressing (HP) method.

Eventually, Si2N2O is in-situ fabricated by nitridizing a powder mixture of Si and SiOor via Self-Propagating High-temperature Synthesis (SHS) [13,14]. In this method, usually much of Si3N4 is produced during the fabrication process, as well as residual Si and SiO2 due to incomplete reaction with each other. Properties of Si2N2O will be remarkably influenced by minor amounts of other phases, such as Si3N4, Si, SiO2 and oxide additives [15]. Wu et al. [16] fabricate Si2N2O ceramic without presence of any kind of secondary phases by in-situ reactive method with nitridizing a powder mixture of Si and SiO2 and multi-step sintering approach. However, this method leads to Si2N2O phase along with high percentage of porosity, which could affect the final properties.

Spark plasma sintering (SPS) is a new powerful pressure sintering method which applies high electrical energy in a short time directly to voids between powder particles and utilizes the high energy of plasma (generated momentarily by spark discharges between the particles) to achieve high thermal diffusion [14]. It is therefore capable of fabricate highly dense compacts at temperatures lower than those of conventional sintering methods in a short period of time which ranges between 5 and 20 min. There are several published previous literatures of SPS that discuss some of the recent advances that have occurred during the past few years in reactive synthesis of bulk materials by SPS [17-19].

In the present work, a highly dense Si2N2O ceramic without existence any kind of secondary phases is fabricated by in-situ reactive synthesis by SPS. The influence of different oxide (MgO and Y2O3) additives on the formation of Si2N2O powders was compared. Phase transformation and densification mechanisms in SPS process were also studied. Finally, the photoluminescence Properties of Si2N2O phase was investigated.


Fabrication of Si2N2O

In order to increase the contact of specific surface of the raw material and improve the additive distribution, mixing of raw materials was carried out as follows. Silica sol was prepared after mixing of 22.1 ml tetraethylorthosilicate (TEOS; Merck), 22.1 ml ethanol (96%<; Merck) and 250 ml distilled water. 4 ml HCl (Merck) and 25 ml HNO3 (Merck) were added as catalysts. 2 wt%. MgO (>99% purity; Aldrich Chemical Company) and 2 wt% Y2O3 (>99% purity; Aldrich Chemical Company) as sintering aids were dissolved in stirring solution after 30 min. Commercial nanosized amorphous Si3N4 powder (>99% purity, ~20 nm, BET surface area= 61.2 m2/g; HeFei Kaier Nanometer Technology Development Co., Ltd., Anhui, China) was added into stirred solution gradually. The compositions of the mixtures used are tabulated in Table 1.

After aging at 60 oC and formation of gel, specimens were dried at 80 oC. After being sieved, the powder was loaded into a graphite die with an inner diameter of 20 mm, and then sintered by SPS (SPS10-60, Iran) at a temperature of 1550°C and 1750°C (heating rate of 100 °C/min) for 40 min under 50 MPa uniaxial pressure under 0.1 MPa fluid nitrogen gas. Finally, samples were ground and then polished on both sides.

Characterization of Si2N2O

Relative bulk density of the samples are measured by Archimedes method using distilled water, and then the total porosity is calculated according to the relative density and theoretical density of the Si2N2O (2.81 g/cm3).

Microstructure and morphology were characterized by field emission scanning electron microscopy (FE-SEM, MIRA 3 TESCAN, South Korea) equipped with electron dispersive spectroscopy (EDS). Phase composition of the sintered samples is identified by X-ray diffraction (XRD, PW1800, Philips, Netherlands). The X-rays were produced using a sealed tube and the wavelength of X-ray was 0.154 nm (CuKα). The XRD traces were recorded in the ٢θ range of ١٠-٨٠° (step size of ٠.٠٤ and scan rate of ٠.٠2°/min).

The distribution of secondary phase was studied using backscattered electron (BSE) detector with 0.1 atomic number resolution from the polished surface of samples.

Raman spectra were taken on dispersive Raman microscopy (BRUKER, Germany, model: Senterra) equipped with CCD detector and Laser wave number of 785nm. The photoluminescence (PL) emission and excitation spectra were recorded at a room temperature using a Shimadzu RF-5301 PC spectrofluoro-photometer. The excitation source was a Xenon lamp. The diameter of the beam focus was about 1 μm. According to calculated optical band gap of Si2N2O (5.1 eV [20]), two excitation wavelengths 240 and 580 nm were selected to study of photoluminescence properties.


Structural features of synthesized specimens

Fig. 1 displays XRD patterns of MgO added synthesized powder. It was revealed from the pattern, that the structural features of synthesized powder are completely amorphous.

As mentioned above, oxide additives that make a liquid phase with the SiO2, should enhance the dissolution of Si3N4 and formation rate of Si2N2O. The type, amount and distribution of metal oxide additives determine the formation temperature, the quantity and viscosity of the liquid phase. Nevertheless, the proper distribution of additive lead to reduction of required sintering aids and sintering time to fully convert to Si2N2O. Fig. 2a shows FE-SEM micrograph of agglomerated synthesized powder. Dissolution of additive in SiO2 solution is caused relatively uniform distribution (Fig. 2b). Uniform distribution of additives in silica sol and using of nanopowder could increase the surface contact of raw materials and improve the kinetic of reactions, finally.

Phase transformation in SPS process

AS specimen

Based on the thermodynamic data, Si2N2O could formed above 1200 °C [15, 21]. However, the X-ray results for specimen AS indicates that no Si2N2O is formed at 1550 °C (see Fig. 3). It was revealed from the pattern that the sample consists of α-Si3N4 phase according to JPCDS card No. 09-0250 and moreover, β-Si3N4 (XRD JPCDS card No. 072-1308) as secondary phase and some remained glassy phase. Increasing the sintering temperature to 1750 oC caused to nucleation of Si2N2O (XRD JPCDS card No. 072-1307). Since, SiO2 have the melting point higher than 1600 oC, consequently, viscous liquid is formed around Si3N4powder. Si3N4 is dissolved and reacted with the Si-O liquid and Si2N2O nucleates and grows on the surface of remained Si3N4. Despite to the previous published literatures [11, 12, 22], Si2N2O was formed without additive in SPS process at a relatively short time. As regards Si-O viscous liquid at the temperature of 1750 oC, the growth of Si2N2O stops.

ASY specimen

Fig. 4 reflects XRD patterns of ASY specimen that is sintered at different temperature. As can be seen from the pattern, Si2N2O was formed as the secondary phase at temperature of 1550 °C, however after increasing temperature to 1750 °C, Silicon oxynitride phase was not formed.

In the presence of a liquid phase obtained by the addition of metal oxide (MexOy), the formation reaction of Si2N2O can be described as the following reaction [12, 22]:

The synthesis/sintering process of Si2N2O involves a liquid phase sintering mechanism. A liquid phase is formed by reaction of the metal oxide additives and SiO2. Then Si2N2O is formed through Si3N4 dissolving and reacting with the SiO2 component of the liquid phase.

Unlike conventional sintering method, Si2N2O was formed by SPS at 1550 oC, without the presence of liquid phase. Fan et al. [23] was suggested a model for the crystallization mechanism of Si2N2O without any liquid phase from amorphous Si3N4 nanopowder in SPS process which, slightly modified, should be applicable in the present case. A part of nitrogen atoms in the amorphous Si3N4 are replaced by the oxygen atoms presented in Y-Si-O dried sol, and consume in the process of sintering under vacuum. A mixed Si-N4-n-Otetrahedra amorphous structure is formed by the diffusion of oxygen atoms into the inside of the amorphous Si3N4 powder, and the oxygen and nitrogen content are in gradient distribution. Therefore, Si2N2O crystals were nucleate at the position where the tetrahedra structure is similar to that of Si2N2O, and distribute discontinuously.

At higher temperature, Y2Si2O7 phase was formed in the sample as a secondary phase beside Si3N4 phase (Fig. 4). Consequently, Si2N2O could not be formed at 1750 oC. BSE micrograph and EDS results from ASY polished surface are shown in Fig. 5. In this micrograph, bright spots can be considered in the dark background. The EDS results indicated that the bright spots have the yttrium. Traces of yttrium cannot be detected in dark area. So these results confirm the fact that Y2O3 with SiO2, create a eutectic transformation higher than 1660 °C [24], and contribute to increase the density of the sample (3.2 g/cm3) because of the liquid sintering. Therefore, Y-Si-O dried sol was crystallized to Y2Si2O7 after being sintered at 1750 oC and reactive sintering did not occurred. Accordingly, it seems no free oxygen remained in structure to react with Si3N4.

ASM specimen

Fig. 6 shows XRD patterns of ASM specimen which is sintered at 1550 and 1750 oC for 40 min. Si3N4, Si2N2O and forsterite (Mg2SiO4) phases were identified after being sintered at 1550 oC. Comparing results with the specimens AS and ASY revealed that the presence of MgO could enhance the rate of reactive sintering and formation of Si2N2O in SPS. Si2N2O phase was formed completely and there is not any trace of raw materials for specimen ASM that have been sintered by SPS at 1750 ºC. It appears clearly that the phase transformation progress is also very fast in the SPS process.

Fig. 7 gives the Raman spectra of the amorphous ASM synthesized powder and the sample sintered by SPS at 1750oC. The spectrum of the amorphous synthesized powder implies the lack of long range order. Three peaks at about 110, 181, and 251 cm-1 are assigned to the Si2N2O compound [25]. The Raman peak at 458 cm-1, assigned to amorphous SiO[23] . So small amount of unreacted SiO2 remain in structure that could not be detected based on the accuracy of the XRD pattern. The mechanism can be due to the lack of nitrogen in structure.

The density of ASM specimen was 2.8 g/cm3. It is very close to the theoretical density of Si2N2O (>99.5% of theoretical density). FE-SEM micrograph of fracture surface of ASM specimen is shown in Fig. 8. So adding MgO could not only increases the reaction rate to the formation of pure Si2N2O structure, but also creates a full density sample.

Mechanisms of formation of pure Si2N2O in SPS process

The phase transformations/reactions that occur in the SPS process are controlled by the same mechanism as in conventional hot pressing. A solution-diffusion-reprecipitation mechanism with higher rate was take place. This can be ascribed to the dissolution and diffusion processes being accelerated by the pulsed electric field. Wang et al. [26] have suggested a model for the microstructural evolution of the present system (ASM specimen). First, Si3N4 is dissolved into Si–Mg–O Liquid. Secondly, Once a sufficient supersaturation of the liquid is attained, Si2N2O nucleates and quick grows in the liquid, then, the degree of liquid supersaturation with (Si,N,O) is reduced, and the growth speed of Si2N2O is therefore considerably decreased.

Upon the formation of a liquid phase based on Si–Mg–O, Si3N4 will dissolve into this liquid. It is known that the solubility of a particle in a liquid increases with reducing the size of the particle. Therefore, using of Si3N4 nanoparticle could enhance the rate of dissolution. These processes involve the reaction of Si3N4 grains and liquid phase interfaces, and diffusion of the (Si, N) ions in the liquid. It has been established that the former is the rate-controlling process [27]. Thus it can be generally expected that the time necessary for the liquid to become supersaturated will be controlled by the Si3N4–liquid phase interface reaction.

Junting et al [28], have confirmed the complex crystallization and phase transition during the liquid phase sintering of amorphous nano-sized silicon nitride powders. At first, amorphous silicon nitride is converted to equiaxial α-Si3N4. Then, after the formation of β-Si3N4 from α-Si3N4, Si2N2O heterogeneously nucleated on the surface of Si3N4.

Si2N2O can be described as being built up structurally by distorted SiN3O tetrahedra, linked together to give an infinite three-dimensional network [29, 30]. Si and nitrogen atoms are situated in an infinite two-dimensional puckered layer linked by an oxygen plane (typically the (200) plane). α- and β-Si3N4 are composed of SiN4 tetrahedra. In Si3N4, there similarly exists the Si–N puckered ring of infinite plane (typically such as the (1010) plane). Replacing nitrogen in a SiN4 tetrahedron of Si3N4 by oxygen will give a unit of SiN3O, which is the structural unit of Si2N2O. Thus it is quite reasonable to propose that any part of the surface of a β-Si3N4 grain which is in contact with the liquid will be eligible for formation of Si2N2O on β-Si3N4 particle surfaces [26].

Because of the low solubility of Mg in Si2N2O grains, growth of Si2N2O embryos may induce the liquid surrounding these embryos to be rich in Mg. So the liquid viscosity is reduced locally, which in turn favors the growth of Si2N2O. This is currently described as the catalytic role of metal ions in the formation of Si2N2O.

According to the above description, proper distribution of metal ions in raw materials is the important factor to reducing the time required for fabrication of pure Si2N2O specimen.

Densification mechanisms in SPS process

It is generally proposed that application of mechanical pressure promotes the removal of pores and enhances diffusion (as HP method). However, it is frequently argued that the promoted densification rates stem mostly from the use of direct high energy current pulses.

The fact that full density can be achieved with very limited involvement of phase transformation and grain growth suggests that densification is accomplished mainly via particle re-arrangement assisted by the presence of a liquid phase.

In this particular case, full density was approached within following stages. First, initial particle re-arrangement initiated when an oxygen-rich liquid is formed (MgO-SiO2 eutectic liquid). Then Extensive particle re-arrangement effected by grain boundary sliding. And finally, closed pores will be eliminated. For SPS, the most attractive feature is the extensive second-stage particle re-arrangement that occurs dramatically fast.

As the sintering progresses so rapidly, it is easy to imagine that it is difficult for the liquid to equilibrate, implying that a nitrogen concentration gradient may exist momentarily in the liquid, close to the undissolved Si3N4 particles. The viscosity of such a liquid phase will depend strongly on the applied heating rate, because the liquid viscosity increases rapidly with increasing nitrogen content [31]. A high heating rate reduces the viscosity by raising the non-equilibrium oxygen rich part of liquid to higher temperatures [32, 33].

This phenomenon contributes to enhancing densification during SPS processing of silicon nitride-based ceramics. Due to the high heating rate applied, a concentration gradient is built up in the liquid, so that the liquid formed close to the Si3N4 particles is rich in nitrogen. When specimen rapidly heated, the oxygen-rich part of the liquid is brought up to a high temperature where it has very low viscosity, thus enhancing the particle sliding under compressive stress [34].

The SPS densification of Si2N2O ceramics with MgO additive occurs within minutes, which is much faster than in conventional hot pressing.

Optical emissivity of Si2N2O

The photoluminescence (PL) properties of ASM specimen were started out at a room temperature with two excitation wavelengths of 240 nm and 580 nm (Fig. 9). This result shows that the Si2N2O have a strong, stable blue emission band centered at 455 nm with excitation wavelengths of 240 nm, which is nearly symmetrical in shape. With lower excitation energy (lower than optical band gap) (580 nm), no PL peak is seen in PL spectrum of Si2N2O. Clearly, this emission were from a direct band gap emission and there are no deep-level or trap-level state in electronic structure of silicon oxynitride. These results are in a good agreement with previous computational theoretical studies [1, 9, 20].


A spark plasma sintering process for fabrication of pure dense Si2N2O ceramic was employed and the role of different oxide on the formation of silicon oxynitride was studied. Using of nanopowders and sol gel preparation method for mixing of raw materials lead to homogenous distribution of additives. Silicon oxynitride was formed as secondary phase in AS specimen without any additives. The fully dense pure Si2N2O was fabricated with 2% mol MgO as an additive at 1750 oC after 40 min by SPS. The rapid densification is ascribed to extensive particle re-arrangement effected by grain boundary sliding, and to the creation of a non-equilibrium liquid phase by rapid heating. Si2N2O have a strong, stable blue emission band centered at 455 nm with excitation wavelengths of 240 nm.


The authors declare that there are no conflicts of interest regarding the publication of this manuscript.


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