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Article

Spark Plasma Sintering of SiAlON Ceramics Synthesized via Various Cations Charge Stabilizers and Their Effect on Thermal and Mechanical Characteristics

by
Muhammad Zulqarnain Falak
1,
Bilal Anjum Ahmed
1,*,
Hasan Aftab Saeed
1,
Sajid Ullah Butt
1,
Abbas Saeed Hakeem
2 and
Usman Ali Akbar
3
1
Department of Mechanical Engineering, National University of Sciences and Technology, Islamabad 44000, Pakistan
2
Interdisciplinary Research Center for Hydrogen & Energy Storage (IRC-HES), King Fahd University of Petroleum & Minerals, Dhahran 31261, Saudi Arabia
3
Department of Mechanical Engineering, King Fahd University of Petroleum & Minerals, Dhahran 31261, Saudi Arabia
*
Author to whom correspondence should be addressed.
Crystals 2021, 11(11), 1378; https://doi.org/10.3390/cryst11111378
Submission received: 23 October 2021 / Revised: 7 November 2021 / Accepted: 8 November 2021 / Published: 12 November 2021
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Abstract

:
Oxygen-rich SiAlON ceramics doped with various nanosized metal oxide (MO) stabilizers were synthesized with a view to examine their effect on thermal and mechanical characteristics. The nanosized starting powder precursors comprising Si3N4, AlN, Al2O3, and SiO2 along with oxides of Ba, Y, Mg, La, Nd, Eu, Dy, Er, and Yb as the MO charge stabilizer were employed in developing different SiAlON samples. Ultrasonic probe sonication was utilized to develop a homogenous mixture of initial powder precursors followed by spark plasma sintering (SPS) of the samples at the low temperature of 1500 °C coupled with 30 min of isothermal treatment. Sample compositions (according to general formula of alpha SiAlON: Mm/vv+Si12−(m+n)Alm+nOnN16−n) selected in the present study are represented by m value of 1.1 and n value of 1.6. The synthesized samples were evaluated for their physical behavior, microstructural and crystal structure evolution, and thermal and mechanical characteristics. More specifically, the sintered ceramics were examined by X-ray diffraction and electron microscopy to comprehend and relate the structural characteristics with the densification, thermal conductivity, hardness, and fracture toughness. The high reactivity of the nanopowders and the localized heating provided by SPS resulted in densified ceramics with relative densities in the range of 92–96%. Vickers hardness values were found to be in the range of 12.4–17.0 GPa and were seen to be profoundly influenced by the grain size of the alpha SiAlON (primary) phase. The fracture toughness of the samples was measured to be in the range of 4.1–6.2 MPa·m1/2. SiAlON samples synthesized using Er and Yb charge stabilizers were found to have the highest fracture toughness of 5.7 and 6.2 MPa·m1/2, primarily due to the relatively higher content of the elongated beta phase. While there was no obvious relationship between the thermal conductivity and the alpha SiAlON metal charge stabilizers, the values were seen to be influenced by the grain size of alpha phase where Dy-SiAlON had the lowest thermal conductivity of 5.79 W/m⋅K and Er-SiAlON showed the highest value of thermal conductivity (6.91 W/m⋅K). It was concluded that scientifically selected metal oxide charge stabilizers are beneficial in developing SiAlON ceramics with properties tailored according to specific applications.

1. Introduction

Ceramic materials are extensively employed in industrial applications due to their exceptional wear resistance, stability at elevated temperatures, hardness, and stable physical and chemical properties. Alternately, these ceramics have a highly brittle nature and low fracture toughness, which imposes a severe limitation on their use in many engineering applications [1,2,3]. Manufacturing of products such as cutting tools, turbine blades, and bearings require materials that provide sufficiently good toughness, hardness, high strength, and exceptional resistance to erosion and corrosion. Silicon nitride (Si3N4) is one of the ceramics having excellent hardness and strength while providing high chemical resistance and low density [4,5,6,7,8]. The key to achieving desirable mechanical, physical, and chemical properties is to have fully densified silicon nitride ceramics. The most common challenge in preparing well-densified silicon nitride ceramics is that of restricted diffusion in these materials owing to the highly covalent nature of bonds. Therefore, near-complete densification of these materials requires elevated sintering temperatures, which gives rise to operational complexities. It is due to this reason that metal oxides and different types of additives have been used as synthesizing and densifying agents which help avoid a long duration of synthesis and high temperature complexities. These additions modify the structure of silicon nitride and lead to the creation of SiAlONs [9,10,11,12,13]. In SiAlONs, certain N and Si atoms are substituted by O and Al atoms and the charge neutrality is ensured by the incorporation of a metal cation [3,8,9,14,15]. α-SiAlON and β-SiAlON phases have been frequently reported in literature. Elongated grain morphology in β-SiAlON is known to impart higher fracture toughness to the SiAlON ceramics [6,14,16,17,18,19], while equiaxed morphology of α-SiAlON is known for its high hardness [6,17,20,21]. It has been established that the formation of a eutectic liquid phase in SiAlONs acts as the synthesis aid to facilitate densification behavior of ceramic composites, such as the work reported on SiAlON/ZrB2-SiC composites produced by SPS and hot pressing techniques [22,23]. Employment of SPS as a sintering route has also resulted in an active focus on controlling the grain growth and morphology of the phases evolved. SPS is a relatively new method used to consolidate starting powders by applying a combination of axial pressure and pulsed direct current to the materials placed within a die of graphite. This approach is sometimes also referred to as the field-assisted sintering technique [24]. Due to the short process time and fewer processing steps it requires, this approach is considered as an energy-saving technology [25,26]. The prominent characteristics of the SPS process include localized generation of plasma, focused plasma–material interaction, and uniform yet fast heating and cooling of the sample [11,12,16,17,27,28,29,30,31]. Synthesis of a variety of new ceramic materials such as WC-Co, C3N4-ZrB2–SiC, TiC–Si3N4, TiC–ZrN–C, TiB2-hBN, and TiC-SiCw-WCn via SPS technology have been reported in literature [32,33,34,35,36,37]. Furthermore, synthesis of porous Al2O3-CNT membranes using SPS technology has also been reported in [38].
Various additives have been employed by researchers to achieve desirable physical, thermal, mechanical, and wear-resistant characteristics of SiAlON-based materials [13], [39,40,41,42,43,44,45,46]. Numerous synthesis techniques along with a range of temperatures have been employed to enhance the thermal shock resistance, toughness, hardness, and densification of SiAlON ceramics. Some studies on the synthesis of SiAlONs have been published that have adopted the conventional sintering route and have utilized a variety of rare earth (RE) and alkaline earth (AE) metal cations; however, very limited literature is available on the synthesis of rare earth- and alkaline-earth-doped SiAlONs via the non-conventional sintering technique [41,47,48,49,50,51]. Table 1 summarizes the findings of past research conducted on alkaline and rare-earth-doped SiAlON ceramics. Souza et al. reported the development of alpha-SiAlON/SiC composites through conventional sintering route at a temperature of 1750 °C [52]. With the addition of SiC reinforcement from 0–20 wt.%, the hardness values were measured to be 12–18.9 GPa. The undesirably low hardness values at higher SiC concentrations were attributed to a reduction in relative density which decreases from 95.4% at 0 wt.% of SiC to 88.3% at 20 wt.% of SiC. Such a drastic drop in relative density can be attributed to the decrease in the amount of additives with the increase in SiC reinforcement, thereby decreasing the eutectic liquid phase, which adversely affects hardness.
Cai et al. reported work on nitrogen rich Ca-SiAlONs while incorporating CaH2 as the source for metal cation, which resulted in the elongated morphology of α-SiAlON [53]. Synthesis of Y/Ca doped α-SiAlON was carried out by Yi et al. using the SPS technique at 1600 °C [54]. A transformation of an α to β phase was reported for Y-α-SiAlON in the range of 1400–1500 °C. On the other hand, there was no apparent α to β transition for Ca–α-SiAlON even at 1600 °C. Vickers hardness values of 19.95 GPa (for Ca-SiAlON) and the 18.56 GPa (for Y-SiAlON) were reported. Xiong et al. reported the development of transparent Mg-stabilized SiAlON ceramics using the SPS technique [55]. It was further explained that the densification and α/β phase ratio had a major influence on the mechanical and optical characteristics of Mg-SiAlONs. Maximum values for optical transmission, surface hardness, and fracture toughness were 66%, 21.4 GPa, and 6.1 MPa·m1/2.
Jojo et al. synthesized Y-doped silicon nitride and aluminum nitride ceramics using the SPS technique, where Y content was varied from 3–7 vol% [56]. It was measured that a sample doped with 7 vol% Y resulted in the best Vickers hardness and fracture toughness values both at 1600 °C and 1675 °C. Ye et al. used 5 wt.% barium aluminosilicate (BAS) as the sintering aid to synthesize Y-α-SiAlON at 1600 °C to yield the maximum hardness of 19.2 GPa [57]. Similar results were published by Wang et al. [58]. ZrB2–ZrC–SiC composites were developed by Akin and Goller at 1750 °C for isothermal holding time of 300 s by SPS. The results showed improvement in densification while the surface hardness was observed to decrease by increasing ZrC concentration. α-SiAlON/ZrC and α-SiAlON/TaC composites were developed by Nino et al. at 1600 °C using the hot pressing technique [59]. At 1600 °C, the β-SiAlON phase precipitated from the α-SiAlON phase, resulting in improved Young’s modulus.
Ahmed et al. reported the development of Ca-α-SiAlON samples at 1500 °C using SPS [12]. The α/(α+β) phase boundary was examined. Compositions with higher oxide content were shown to help produce the β-SiAlON phase, thereby enhancing the fracture toughness of the samples. The Ca-α-SiAlON/SiC composites were prepared by Khan et al., utilizing the SPS process at 1500 °C with 30 min holding time. Fracture toughness of 7.3 MPa·m1/2 and Vickers hardness of 21.1 GPa was reported [14].
In the present work, various metal cations stabilized oxygen-rich SiAlONs are developed at a low synthesis temperature of 1500 °C by employing the SPS technique. Furthermore, the effect of these metal charge stabilizers on the microstructure, phase evolution, and physical and thermomechanical characteristics is analyzed. Ultrasonic probe sonication is employed to achieve a homogenous mixture of starting powder mixture. The influence of RE and AE MOs as additives is evaluated in an effort to improve the much desired thermal and mechanical behavior of SiAlONs. All precursors used are of a nano-scale size, which facilitates the synthesis at 1500 °C. The metal oxide precursors used as the charge stabilizers include BaO, MgO, Y2O3, La2O3, Nd2O3, Dy2O2, Er2O3, Yb2O3, and Eu2O3.

2. Materials and Methods

In the preparation of SiAlON samples, the powder blend of the initial precursors was reacted together. SiAlON samples were synthesized with commercially procured materials SiO2 (~50 nm, Sigma-Aldrich, St. Louis, MO, USA), AlN (less than 100 nm, USA, Sigma-Aldrich, St. Louis, MO, USA) and Si3N4 (~300 to 500 nm, UBE Industries, SN-E10, Tokyo, Japan). Metal oxides procured from USA, Sigma-Aldrich, included BaO, with purity over 99 percent, while the remainder of the pure oxides having a purity of greater than 99 percent were purchased from Champur, Germany. Table 2 enlists the weight percent of each powder precursor used to prepare the respective SiAlONs. The general formula utilized for the synthesis of SiAlONs is M(m/v)v+Si12-(m+n)Al(m+n)OnN16−n, where M represents the metal cation. The variables n and m indicate Al–O and Al–N bonds, respectively. In the general formula n+m: Si–N bonds are replaced by m (Al–O) bonds, while v represents the valency of metal cation M (which is +3 for all the metal cations except for Ba and Mg, for which it is +2). In this study, the composition represented by m = 1.1 and n = 1.6 was selected for the synthesis. VCX 750 probe sonicator was used to homogenize the powder mixture in the ethanol medium for up to 20 min. Probe-sonicated powder mixture was then dried at 90 °C for a period of 24 h in an oven. The dried powder mixture of initial powder precursors was sintered using FCT Systeme, HP D5 SPS machine. Uniaxial compression pressure of 50 MPa was maintained constant throughout the process for the powder mixture enclosed in a 20 mm graphite die [11,12,13,14,26,64]. The maximum sintering temperature of 1500 °C was employed whereas the holding time of 30 min was used at the maximum temperature for all the samples [13,42]. A high heating rate of 100 °C per minute and a constant vacuum of 5 × 10 − 2 mbar was maintained for the samples. SPS densification curves for the selected samples highlighting the major densification stages are shown in Figure 1. The temperature corresponding to the initiation of various stages are illustrated as an inset in Figure 1. Sintered samples were ground off using SiC abrasive grinding papers to remove the graphite layer and were subsequently grounded and polished using diamond disks and a diamond polishing medium.
The fractured surface morphology of the sintered samples was examined using a field emission scanning electron microscope (Lyra3, FESEM, Czech Republic, Tescan) in the backscattered mode. It was equipped with the dispersive energy X-ray spectrometer to monitor the elemental distribution. Phase analysis was performed using Miniflex powder X-ray diffractometer where Cu source having a wavelength of 0.15416 nm, 10 mA current, and 30 kV voltage were set as the equipment parameters. Archimedean principle was employed for measuring the density of the sintered samples. In order to calculate the density values, a density balance kit (Xing Yun, Model # 2019129071) was used with deionized water as the sample immersion medium. The density of the samples was calculated on average by five measurements. Theoretical densities of the samples were calculated using the weight percent of the initial precursors in a sample (see Table 2) and the rule of mixtures. To evaluate the Vickers hardness of SiAlON samples, a 10 kg (98.06 N) load was applied by means of a universal hardness test ZwickRoell, ZHU250. Evan’s equation (Equation (1)) was used to measure the fracture toughness (KIc) of the samples. In this equation, ‘H’ represents Vickers hardness, ‘a’ represents half of the average diagonal length (microns) and ‘c’ is the average length of the cracks (microns) [65]. C-Therm, TCi, Canada was used to evaluate the thermal conductivity of the specimens at room temperature.
K IC = 0.16 c a − 1.5 Ha 0.5
SPS densification curves of selected samples highlighting various stages of synthesis process are shown in Figure 1. Though the generic densification behavior of all the samples was similar, the solution–diffusion–precipitation stage was seen to be influenced by the melting temperature of the metal oxide precursors. In the case of MgO having the highest melting temperature of 2852 °C, the solution–precipitation state started at around 1357 °C. In contrast, for Nd2O3 (having the lowest melting temperature), the solution–precipitation stage started at around 1185 °C. Furthermore, despite the difference observed in the onset temperature of various stages, the initiation of the final coalescence stage remained the same for all the samples. A similar observation was reported by Hakeem et al. in their study on the densification behavior of alpha SiAlON ceramics [61].

3. Results and Discussion

3.1. Phase Evolution and Microstructure Analysis

In this work, commercially available powders were procured. Chemical compositions of the SiAlON samples, along with the respective weight percent of the starting powders and their characteristics are expressed in Table 2. Nine samples were synthesized using metal oxides, namely: La2O3, Nd2O3, Eu2O3, Dy2O3, Er2O3, Yb2O3, MgO, BaO, and Y2O3. As shown in the densification plot of spark plasma sintered samples (Figure 1), the evolution of SiAlON phases was observed to take place in the range of ~1000–1500 °C. The solution–precipitation process initiated at around ~1200 °C and continued until almost 1500 °C. Similar observation has been reported in previous studies [13,19,28,66]. It is believed that the nitride powders reacted with the oxide precursors to form the oxynitride eutectic liquid phase, which facilitated the densification of SiAlON ceramic. The amount of the eutectic liquid increased with the rise in temperature and complete conversion into SiAlON was achieved at 1500 °C.
Additionally, the present study was aimed at determining the effect of alkaline and rare earth stabilizing cations on phase formation, microstructure evolution, and thermal and mechanical properties of SiAlON samples. The XRD patterns of the synthesized samples labelled with the corresponding phases are depicted in Figure 2. Alpha SiAlON (ICD# 00-042-0252) phase was seen to be present in all the samples as the major phase, along with beta SiAlON (ICD# 00-048-1615) as the minor phase. The presence of a major alpha phase coupled with a minor beta phase in all the samples confirms the fact that the initial composition selected for this study belongs to the oxygen-rich alpha/beta region and that the replacement of cations did not have any significant effect on the single-phase alpha stability regime. Nevertheless, it was seen that the cationic size of the stabilizing cations did influence the XRD peak intensities and the peak positions. For instance, with the change in rare earth cationic size (La (250 pm) having clear discrete cationic size as compared to Nd (229 pm)) the alpha reflexes shifted to a slightly lower 2-theta value, indicating higher accommodation of stabilizing cation within the alpha unit cell. Furthermore, AlN polytype (ICD# 00-042-0161 and ICD# 00-042-0160) reflexes were also observed in some of the samples, as was reported in previous studies as well [61]. Other than this, a few additional reflexes were observed in the sample synthesized using BaO. The additional reflexes were identified as Ba2Si10Al2O4N14 (ICDD# 00–057-0526) phase [61]. BaO having the lowest melting temperature of 1923 °C resulted in the formation of the additional phase. A similar observation was reported by Hakeem et al. [61].
Figure 3 depicts the low magnification fractured surface morphology of SiAlON doped with various cations, all sintered at 1500 °C. As was also observed in the X-ray diffraction plot, the fracture surface of La stabilized SiAlON (Figure 3a) does not show any visible signs of the glassy phase. Highlighted in the micrograph, the fractured surface depicts three distinct features, namely, small alpha grains having equiaxed morphology, beta-SiAlON grains having elongated morphology, and relatively larger AlN polytype grains depicting a flat plate-like fractured morphology. Furthermore, in line with the phase-detection results, the alpha SiAlON is seen as the dominant phase, whereas fewer grains of beta SiAlON and AlN polytype are observed. Figure 3b represents the high magnification image of the area highlighted in Figure 3a. The average grain size of the alpha phase is 290 ± 76 nm. It appears that the La–oxynitride eutectic liquid has facilitated the growth of minor phase(s) thereby restricting the development of the alpha phase.
For Nd-stabilized SiAlON (Figure 3c), in line with the X-ray diffraction results, the fractured surface is dominant with the equiaxed alpha SiAlON grain. At the same time, some elongated grains of beta-SiAlON (as highlighted in the image) are also observed. Again, as per FESEM observations, there were no visible signs of the amorphous glass phase at the grain boundaries. Figure 3d represents the high magnification image of the area highlighted in Figure 3c. The average grain size of Nd-alpha SiAlON is measured to be 242 ± 67 nm. It is evident that unlike the case of La-stabilized SiAlONs, Nd–oxynitride eutectic liquid has promoted the formation of alpha SiAlON grains rather than the polytype AlN phase.
The distinct features as highlighted in the fractography of Eu-stabilized SiAlON (Figure 3e) include small equiaxed grains of alpha phase, elongated interlocking grains of beta phase, dark grey flat plate-like morphology of AlN polytype phase, and the bright white small pockets of intergranular (IG) amorphous glassy phase. Figure 3f represents the high magnification image acquired from a similar region. The average grain size of the alpha phase is 294 ± 71 nm. It is evident that much of the Eu–oxynitride eutectic liquid phase was present as the amorphous grain boundary phase and thereby growth of the well-developed alpha SiAlON phase was restricted.
The fractography of Dy-stabilized SiAlON (Figure 3g) depicts a mixed fracture surface where an equiaxed small alpha SiAlON grains area is surrounded by plate-like morphology of polytype AlN grains representing a transgranular fracture. The high magnification image (Figure 3h) of the same sample also indicates relatively thick fractured grains of beta SiAlONs with a relatively lower aspect ratio. However, any visible sign of the amorphous grain boundary phase is not present. The measured average alpha SiAlON grain size is 185 ± 34 nm.
The fractured surface of Er-stabilized SiAlON (Figure 3i) depicts well developed equiaxed morphology of alpha SiAlON as the dominant phase, along with pockets of beta-SiAlON phase having an elongated morphology. Furthermore, the presence of an intergranular glassy phase having a bright white appearance is also very evident. The high magnification image (Figure 3j) of the same sample further indicates that the amount of amorphous phase was minimal and is mainly present at triple point junctions and in between the elongated grains of beta SiAlON. The average alpha SiAlON grain size is measured to be 711 ± 106 nm.
In Yb-stabilized SiAlON (Figure 3k), the equiaxed morphology of alpha SiAlON phase is seen to be the dominant morphology whereas small regions having elongated morphology of beta SiAlON phase are also evident. The high magnification image (Figure 3l) of the same sample provides the evidence of glassy phase present within the vicinity of interlocking elongated beta SiAlON grains. The appearance of the amorphous grain boundary phase is seen to be bright white in color as highlighted in Figure 3l. The average size of alpha SiAlON grains is 538 ± 109 nm.
The general appearance of the fractured surface of Ba-stabilized SiAlON (Figure 3m) is dominant with equiaxed alpha SiAlON grains, while a few larger dark grey grains of AlN polytype phase are also observed. No evidence of glassy grain boundary phase is observed. The high magnification image (Figure 3n) reveals a transgranular fracture mode within the polytype AlN grain. The measured average size of alpha SiAlON grains is 238 ± 43 nm.
The fracture surface of Y-stabilized SiAlON (Figure 3o) generally depicts the equiaxed appearance of alpha SiAlON grains, while small regions having elongated beta SiAlON morphology are also observed. The elongated morphology of the beta phase is more visible in the high magnification image (Figure 3p). An entrapped glassy phase in small amounts, having a brighter appearance, is also seen within the vicinity of elongated beta SiAlON grains. The average size of alpha SiAlON grains is measured to be 535 ± 112 nm.
The general appearance of the fractured surface of Mg-stabilized SiAlON (Figure 3q) is dominant with equiaxed alpha SiAlON grains while some larger dark grey grains of AlN polytype phase having a plate-like morphology are also observed. A transgranular fracture mode within the polytype AlN grain is quite evident, while no signs of the amorphous grain boundary phase are visible. The average size of alpha SiAlON grains is 277 ± 50 nm.

3.2. Densification, Mechanical, and Thermal Properties

The thermal and mechanical properties and the densities of spark-plasma-sintered SiAlON ceramic samples are listed in Table 3. Generally, it is observed that the density value has increased with the increase in the atomic number of charge stabilizing element (used as charge balance in the starting composition). This finding is in line with the previously reported work on SiAlON-based systems [61]. Any obvious sign of porosity has not been observed in the microscopic examination, which conforms with the comparatively good relative densification of the samples, specifically in reference to the relatively low sintering temperature of 1500 °C. Although it is an established finding that high densification is associated with grain growth in the conventional sintering processing of SiAlON ceramics, in the present study grain growth was generally well controlled due to the much faster heating and cooling rates achieved via SPS. Unique and localized heating provided continuous dissolution and reaction of nanosized precursors in the oxynitride eutectic liquid, thereby playing a significant role in attaining near full densification at low temperature. Any direct relationship of thermal properties with the atomic size of charge stabilizers, as in the case of density, was not observed.
The thermal conductivity of SiAlONs has shown a mixed behavior where values were measured to be from 5.79 to 6.91 W/m⋅K. Generally, the thermal conductivity values are influenced by the grain size where Dy-doped SiAlON, having the smallest average grain size of 185 nm, show the lowest thermal conductivity of 5.79 W/m⋅K; while Er-doped SiAlON, having the largest average grain size of 711 nm, result in the highest thermal conductivity of 6.91 W/m⋅K. Huicong et al. reported that grain boundaries generally act as a hindrance in thermal transmission, thereby causing a decrease in thermal conductivity with decreasing grain size [67]. Since any significant variation in the thermal conductivity values has not been apparent, it is believed that other parameters such as porosity level and amount of minor phases have not had a significant role in influencing the thermal behavior of synthesized materials [19,68,69,70].
The measured hardness of all the samples is in the range of 12.4–17.0 GPa. Hakeem et al. reported hardness values in the range of 15.5–20.8 GPa (HV10) for nitrogen-rich alkaline-earth- and rare-earth-doped SiAlONs [61]. Relatively lower hardness values observed in the present study are ascribable to the initial composition selected for the synthesis, which belongs to the oxygen-rich region on the alpha SiAlON plane. Generally, the hardness of the SiAlON samples was found to be profoundly influenced by the alpha SiAlON grain size. In the rare earth series, it was observed that Dy-doped SiAlON, having the smallest average grain size of 185 nm, has the highest hardness of 17.0 GPa. Er- and Yb-doped SiAlONs, having the average grain size values of 711 nm and 535 nm, have relatively lower hardness values of 15.1 and 15.6 GPa, respectively. The presence of grain boundary liquid in Er- and Yb-doped SiAlONs suggests that rare earth SiAlONs having the lowest ionic radius have not only promoted the formation of the eutectic liquid phase but have also favored the growth of alpha SiAlON grains. In the alkaline earth series, Ba-SiAlON was measured to have the lowest hardness, primarily due to the presence of barium aluminosilicate phase in the matrix. The measured fracture toughness values of all the samples vary from 4.1 to 6.2 MPa⋅m1/2. It is seen that a higher ionic radius promotes the formation of AlN polytype phase which ultimately lowers the fracture toughness of the samples. Biswas et al. reported AlN fracture toughness values in the range of 2.4–3.9 MPa⋅m1/2 [71], which supports the lower fracture toughness values observed in the present work. Furthermore, Er- and Yb-doped SiAlONs having well developed beta SiAlON regions and entrapped grain boundary phases are found to have the highest fracture toughness values of 5.7 and 6.2 MPa⋅m1/2, respectively. Plastic deformation of the secondary phase crystals and the grain boundaries are reported to be prominent reasons for improved fracture toughness [6,13,14,28,68,72,73,74]. It is further reported in the literature that cracks will be inclined to propagate along the grain boundary interface when the secondary phase grains or grain boundary glassy region is well connected to the matrix grains [13,28,68]. With the results of the present work, very well suited SiAlON ceramics could be developed for the drilling and cutting tools industry. In today’s competitive world, it is highly desirable to have an economically viable manufacturing route. In comparison with the already published literature, it is apparent that well suited SiAlON-based cutting tools can be developed economically via non-traditional sintering techniques (such as SPS) at considerably lower sintering temperatures.

4. Conclusions

Metal-oxide-stabilized SiAlON ceramics having the m value of 1.1 and n value of 1.6 were synthesized at the sintering temperature of 1500 °C. Thoroughly densified SiAlON ceramics having values in between 3.17–3.92 g/cm3 were developed by employing a nano-sized starting powder mixture coupled with the unique and efficient heating mechanism provided by spark plasma sintering. The thermal conductivity values were found to vary in the narrow range of 5.79–6.91 W/m⋅K, where the Er-stabilized sample had the highest value owing to its largest grain size. The hardness and fracture toughness values were measured to be in the range of 12.4–17.0 GPa and 4.1–6.2 MPa⋅m1/2, respectively. The high fracture toughness of Er- and Yb-doped SiAlON was attributed to the presence of elongated beta SiAlON grains in the alpha matrix. It is concluded that SiAlON ceramics stabilized with various charge stabilizers having diversified thermal and mechanical properties could be utilized for products requiring high contact resistance such as bearings, cutting tools, and automotive brake pads.

Author Contributions

Conceptualization, B.A.A., A.S.H.; Data curation, M.Z.F. and S.U.B.; Formal analysis, B.A.A. and H.A.S.; Investigation, M.Z.F., B.A.A., A.S.H. and U.A.A.; Methodology, M.Z.F., B.A.A., S.U.B. and A.S.H.; Project administration, B.A.A. and H.A.S.; Resources, A.S.H. and U.A.A.; Supervision, B.A.A., H.A.S. and S.U.B.; Writing—original draft, M.Z.F. and B.A.A.; Writing—review & editing, B.A.A., H.A.S., S.U.B., A.S.H. and U.A.A. All authors have read and agreed to the published version of the manuscript.

Funding

This research received no external funding.

Institutional Review Board Statement

Not applicable.

Informed Consent Statement

Not applicable.

Data Availability Statement

Not applicable.

Conflicts of Interest

The authors declare no conflict of interest.

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Crystals 11 01378 g001 550
Figure 1. Spark plasma sintered densification behavior of synthesized ceramics.
Figure 1. Spark plasma sintered densification behavior of synthesized ceramics.
Crystals 11 01378 g001
Crystals 11 01378 g002 550
Figure 2. XRD patterns of various synthesized SiAlONs using alkaline earth and rare earth metal cations.
Figure 2. XRD patterns of various synthesized SiAlONs using alkaline earth and rare earth metal cations.
Crystals 11 01378 g002
Crystals 11 01378 g003a 550Crystals 11 01378 g003b 550Crystals 11 01378 g003c 550
Figure 3. FESEM micrographs representing fractured surfaces of SiAlONs doped with (a,b) La, (c,d) Nd, (e,f) Eu, (g,h) Dy, (i,j) Er, (k,l) Yb, (m,n) Ba, (o,p) Y, and (q) Mg, cations.
Figure 3. FESEM micrographs representing fractured surfaces of SiAlONs doped with (a,b) La, (c,d) Nd, (e,f) Eu, (g,h) Dy, (i,j) Er, (k,l) Yb, (m,n) Ba, (o,p) Y, and (q) Mg, cations.
Crystals 11 01378 g003aCrystals 11 01378 g003bCrystals 11 01378 g003c
Table
Table 1. Results and literature review of different studies on SiAlONs of various alkaline earth and rare earth metal additives.
Table 1. Results and literature review of different studies on SiAlONs of various alkaline earth and rare earth metal additives.
S/NoSample NameTemperature (°C)Holding TimePressure/Synthesis MethodHv
(GPa)		KIC
(MPa·m1/2)		Ref
1Beta-SiAlON* NA* NA* NA19.92.9[60]
2Alpha-SiAlON* NA* NA* NA15.95.9[60]
3Ytterbium-alpha-SiAlON150030 minSPS
50 MPa		20.66.3[61]
4Calcium-alpha-SiAlON175060 minHP
20 MPa		19.46.1[58]
550 wt.% TiN-alpha-SiAlON1600* NASPS
100 MPa		15.77.9[25]
63 wt.% MgO-beta-SiAlON+ 7 wt.% Y2O31750150 minHP
30 MPa		20.96.1[62]
730 wt.% Silicon carbide-calcium-Alpha-SiAlON150030 minSPS
MPa		21.17.3[14]
85 wt.% BAS-alpha-SiAlON18005minSPS
25 MPa		19.26.8[57]
9Magnisium-alpha-SiAlON185060 minSPS
30 MPa		21.46.1[55]
10Calcium-magnisium-alpha-SiAlON175060 minHP
20 MPa		19.75.8[58]
11Rare earth-Silicon carbide-beta-SiAlON1950NA*Cold pressed19.54.2[63]
12Calcium-alpha-SiAlON140010 minSPS
40 MPa		19.9-[54]
* NA—not available.
Table
Table 2. Starting chemical compositions of SiAlON ceramics along with the weight percent of respective powder precursors employed in the synthesis.
Table 2. Starting chemical compositions of SiAlON ceramics along with the weight percent of respective powder precursors employed in the synthesis.
Sample NoChemical FormulaCharge StabilizerMetal Oxide (MO)Melting Temp of MO (°C)MO Size (nm)Si3N4 (wt.%)AlN (wt.%)MO (wt.%)SiO2 (wt.%)Al2O3 (wt.%)
1Mg0.55Si9.3Al2.7O1.6N14.4MgMgO2852503.8673.9216.293.732.20
2Ba0.55Si9.3Al2.7O1.6N14.4BaBaO192320013.2666.7014.703.371.98
3Y0.367Si9.3Al2.7O1.6N14.4YY2O32425506.9871.5215.763.612.12
4La0.367Si9.3Al2.7O1.6N14.4LaLa2O32315309.7769.3815.293.502.06
5Nd0.367Si9.3Al2.7O1.6N14.4NdNd2O322338010.0969.3815.293.502.06
6Eu0.367Si9.3Al2.7O1.6N14.4EuEu2O323506010.5569.3815.293.502.06
7Dy0.367Si9.3Al2.7O1.6N14.4DyDy2O324085511.1869.3815.293.502.06
8Er0.367Si9.3Al2.7O1.6N14.4ErEr2O323444011.4769.3815.293.502.06
9Yb0.367Si9.3Al2.7O1.6N14.4YbYb2O3235510011.8269.3815.293.502.06
Table
Table 3. Physical, mechanical, and thermal properties of Spark-Plasma-Sintered samples prepared at 1500 °C.
Table 3. Physical, mechanical, and thermal properties of Spark-Plasma-Sintered samples prepared at 1500 °C.
Alkaline Earth StabilizersRare Earth Stabilizers
Sample Id’sBaMgYLaNdEuDyErYb
Density (g/cm3)3.423.173.233.473.533.593.673.783.92
Relative Density (%)959692939192929293
Thermal Conductivity (W/mK)6.046.806.496.136.096.045.796.916.67
Hardness Hv10 (GPa)12.4 (5)16.9 (4)15.5 (4)16.6 (5)16.2 (6)16.3 (4)17.0 (6)15.1 (4)15.6 (5)
Fracture Toughness KIc (MPa.m1/2)4.1 (4)4.4 (6)5.1 (5)4.5 (7)4.3 (2)4.5 (2)4.2 (2)5.7 (7)6.2 (6)
(±) is represented by values in the curved brackets.
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Falak, M.Z.; Ahmed, B.A.; Saeed, H.A.; Butt, S.U.; Hakeem, A.S.; Akbar, U.A. Spark Plasma Sintering of SiAlON Ceramics Synthesized via Various Cations Charge Stabilizers and Their Effect on Thermal and Mechanical Characteristics. Crystals 2021, 11, 1378. https://doi.org/10.3390/cryst11111378

AMA Style

Falak MZ, Ahmed BA, Saeed HA, Butt SU, Hakeem AS, Akbar UA. Spark Plasma Sintering of SiAlON Ceramics Synthesized via Various Cations Charge Stabilizers and Their Effect on Thermal and Mechanical Characteristics. Crystals. 2021; 11(11):1378. https://doi.org/10.3390/cryst11111378

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Falak, Muhammad Zulqarnain, Bilal Anjum Ahmed, Hasan Aftab Saeed, Sajid Ullah Butt, Abbas Saeed Hakeem, and Usman Ali Akbar. 2021. "Spark Plasma Sintering of SiAlON Ceramics Synthesized via Various Cations Charge Stabilizers and Their Effect on Thermal and Mechanical Characteristics" Crystals 11, no. 11: 1378. https://doi.org/10.3390/cryst11111378

APA Style

Falak, M. Z., Ahmed, B. A., Saeed, H. A., Butt, S. U., Hakeem, A. S., & Akbar, U. A. (2021). Spark Plasma Sintering of SiAlON Ceramics Synthesized via Various Cations Charge Stabilizers and Their Effect on Thermal and Mechanical Characteristics. Crystals, 11(11), 1378. https://doi.org/10.3390/cryst11111378

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