All materials can be broadly classified into three categories: Metal, Ceramic and Polymer. For the better high temperature strength, light weight, low wear rate and high hardness properties make ceramic the material of choice for a wide range of applications . Alumina is one of the most extensively used and cost-effective materials in engineering ceramic family. It is one of the hardest materials and its hardness is just only next to diamond (9 out of 10 in Mohs scale). It has strong ionic interatomic bonding that provides its reputed material features. Several inherent properties such as low thermal conductivity, comparatively high thermal expansion coefficient and pronounced chemical stability make it appropriate to choose for ceramic materials. In the early 70s’ bio-ceramics were employed to perform singular biologically inert roles, such as to provide parts for bone replacement. Alumina (Al2O3) as an inert bio-ceramic has also biomedical application as an alternative to metal alloys for the replacement of hip prostheses and dental implants. However, the low fracture toughness property limits its load-bearing capacity which is the major drawback of it . Like alumina, zirconia is also one of the most versatile of refractory ceramic oxide. An excellent corrosion resistance, strength, toughness and chemical inertness properties make it superior for the ceramic composites at temperature well above the melting temperature of alumina. It needs to be stabilized for avoid cracking under stress conditions. It has three polymorphs: monoclinic (m, up to 1170˚C), tetragonal (t, up to 2370˚C) and cubic (c, up to 2680˚C) . With increasing heating temperature, phases transform from monoclinic to tetragonal zirconia associated with almost 5% volume change   . During cooling to room temperature, tetragonal phase of zirconia transforms into monoclinic phase with expansion of its volume of nearly 3% - 5%. If any stress is applied, the stabilized tetragonal phases of zirconia at room temperature change their phases into monoclinic with expanding their volume by absorbing the energy applied on them and stop the crack to propagate further which is referred to as stress-induced phase transformation of zirconia . Through applying this phase transformation mechanism, it increases the fracture toughness of the composite materials that are generally defined as the toughening mechanism. To retain in tetragonal phase at room temperature, the grain size of zirconia must be smaller than the critical transformation size, below which no phase transformation occurs . Relative distribution of ZrO2 and volume fraction of ZrO2 retained in the metastable tetragonal phase are also responsible for the increases of fracture toughness of the composites. Finer particle size enhances the uniform distribution of both Al2O3 and ZrO2 particles and tetragonal phase retention possibilities of ZrO2 particle . On the other hand, in the case of over-stabilization, the stress required for the phase transformation may be higher than the fracture toughness. That’s why the fracture toughness will be reduced. So, no stabilizer is used in this experimental procedure. Side by side increases the volume percentages of ZrO2 also decreases the percentages of tetragonal ZrO2 retention. So, an optimum amount ZrO2 addition is required for getting the maximum desired properties. Previous research found that the mixture of both monoclinic and tetragonal phases of ZrO2 has provided the maximum fracture toughness in zirconia toughened alumina (ZTA) .
To overcome the shortcomings of alumina ceramics, Alumina-Zirconia (AZ) ceramic composites are extensively explored over the last two decades  . Among these composites, zirconia toughened alumina (ZTA) has been elaborately studied due to its prominent mechanical properties such as high corrosion resistance and chemical stability. Alumina has high hardness and the toughness of the zirconia is very good. Zirconia toughened alumina (ZTA) composite ceramics have the properties of both materials. The performance of zirconia toughened alumina ceramics is much better than the alumina ceramics and the price is much lower than the zirconia ceramics. Upgraded mechanical properties would be found by the incorporation and more homogeneous distribution of zirconia in alumina matrix    . According to application purposes, properties of the ceramics can be tailored to depend on the percentage of the contents. Due to superior mechanical behavior it may be used in both biomedical and engineering applications. The addition of sintering aid (MgO, CaO) as a small amount increases the densification process of the Alumina-Zirconia ceramic composites by lowering the sintering temperature as well as decreases the grain growth of Alumina resulting in a stronger composite formed.
The previous studies emphasized the improvement of mechanical properties of ZTA by using stabilized zirconia as reinforcement  . The analysis also reported that stabilized zirconia has a great effect (impart toughening mechanism) on the mechanical properties. But the effect of unstabilized zirconia on the properties of ZTA is not extensively studied particularly using the powder compaction method. In this investigation, optimization of the composition will be done to get maximum fracture toughness, microhardness, flexural strength and density by varying the volume percentage of unstabilized zirconia. To get the proper output conventional powder compaction method is applied for the sample preparation. Absolute ethanol is used as a liquid media for uniform mixing of the raw powders during pot milling. A sintering schedule will be followed for all composition of the sample by keeping sintering time and temperature at constant level. That will be an alternative and convenient approach to produce Alumina-Zirconia (Al2O3-ZrO2) ceramic composites which might be used in replace of other traditional ceramic composites rather than cost effectively.
Commercially available ceramic powders such as nanocrystalline alpha-alumina powder (purity 99.9%, average particle size ~150 nm, Advance materials, USA), monoclinic zirconia powder (purity 99.9%, particle size 30 - 60 nm, Advanced materials, USA) and magnesiumoxide (purity > 97%, particle size < 50 nm, RCL Labean Ltd., Thailand) were taken for this work. Here high purity alumina was used as a base material due to avoid the formation of glassy phases on the grain boundaries of ceramic composites. Unstabilized zirconia was incorporated rather than partially stabilized zirconia (PSZ) as it limits the activity of transformation during crack propagation. Different volume percentages of monoclinic zirconia (such as 0, 2, 5, 10, 15 and 20 vol%) and 0.2 wt% of MgO were added to alumina for the fabrication of ceramic materials.
Initially right amount of powder raw materials is taken into a polypropylene pot. Absolute ethanol (Merck, Germany) is used as a solvent media for wet milling. For the homogeneous mixing of the powders 24 hours pot milling is continued by motor driven mill with yttria stabilized zirconia balls as a grinding media. Then the mixture was dried in a vacuum oven (UE600, Memmert, Germany) at 100˚C for 24 hours. The dried mixture was milled in a mortar pestle for more uniform mixing and 5% PVA (polyvinyl alcohol) solution was added as a binder for providing green strength of the samples. After that the blended mixture was unidirectionally pressed in discs (10 mm diameter) at 210 MPa for 120 sec using UTM (FS 300 kN, Testometric Co. Ltd., England). Before sintering in a high temperature heating furnace (BPAN-2010, Micropyretics Heaters International, USA) at 1580˚C for 2 hours at the heating rate of 5˚C/min in a pressure less condition, the green samples were dried at 100˚C for 24 hours in an oven (UE600, Memmert, Germany) for the removal of the containing moisture. During sintering there was maintained a holding period of time (3 hours) at 600˚C for the complete removal of binder from the sample. The cooling rate of the sample from the sintering temperature was comparatively higher (10˚C/min). Single stage sintering cycle of this work is shown in Figure 1.
The density of the sintered body was measured by immersion in distilled water using Archimedes’ principle. At least six samples were considered for density determination of any type of sintered sample and the variation in the density
Figure 1. Typical sintering cycle.
was shown to be within ±1%. Standard Archimedes formula for calculating the density of the sintered sample is as follows:
where, is the density of the sintered sample, is the density of the water, is the mass of the sintered disc, is the mass of the disc in water.
The percentage of total porosity was calculated from the sintered density and the theoretical density according to the standard formula :
where, is the total porosity of the sample, is density of sintered pellet and is the theoretical density for samples.
The microhardness was determined on the polished surface of sintered sample by using microhardness tester (HMV-2 Series, Shimadzu Corporation, Japan) following Vickers indentation approach. This value was measured from the ratio of the applied load to the area of the contact of four faces of the undeformed indenter. Following formula was applied to compute Vickers hardness:
where, Hv is the Vickers hardness (GPa), P is the applied load (N), d is the average length of two diagonals of the indentations (mm).
The porosity dependence Elastic Modulus can also be measured using Dewey-Mackenzie relation :
where, E is the effective elastic modulus of porous composites. Eo is the elastic modulus of the dense composite and is the porosity of the sample.
Fracture toughness of the composite was measured on the polished surface of the sintered composite by Vickers indentation fracture methodusing the followingAnstis equation :
where, KIC, Hv, E, P and C stand for the fracture toughness (MPam½), Vickers hardness (GPa), elastic modulus (GPa), indentation load (MN) and radial crack length (m), respectively. In this case applied load was 20 kg for 15 second (DVK-2, MATSUZAWA). All fracture surfaces were observed in an optical microscope (NMM-800T RF, USA). Before indentation the specimen surface was ground successively using 1200 and 4000 grit SiC discs respectively. Following this, the samples were polished in 6 µm and 1 m diamond paste on a texmet cloth. The reported values were the average of data obtained from six indentation tests.
Crystalline Phases identification was performed on sintered surface by using X-ray diffractometer (XRD) with CuKα radiation (λ = 1.54 Å) (D8 Advance, BRUKER, Germany) technique. The scanning speed was 2˚/min and range of the 2θ value was 20˚ - 70˚. The volume fraction of monoclinic zirconia (Vm) was calculated according to the following equation .
where, I is the integral intensity and the subscripts m and t refer to the monoclinic and tetragonal phase, respectively.
Microstructure of the sample was studied by Scanning Electron Microscopy (SEM). The polished samples were sputter coated with platinum coating in a sputtering for 2 - 3 minutes to make the surface conducting. The specimens were observed by SEM (JEOL-6490, Japan) in secondary electron (SE) mode at 20 KV accelerating voltage. The average grain sizes of alumina and zirconia were measured from the microstructure by using line intercept method. Thermodynamically stable m-ZrO2 and the retention of t-ZrO2 phases were studied following Garvie’s method .
4. Results and Discussion
4.1. Density and Porosity
The following Figure 2 and Figure 3 indicate the variation of the density and porosity of sintered composites as a function of the vol% of zirconia content. The reported values are the average of data found from six pellets. It has been seen that the density of the sintered body increases with increasing zirconia contentand the porosity decreases with increasing zirconia. This is due to the addition of denser zirconia (5.68 g/cm3) into the alumina (3.97 g/cm3) matrix. For the addition of 0 vol% of ZrO2 to Al2O3 matrix, the density of the sample was
Figure 2. Effect of ZrO2 addition on the density of the Al2O3-ZrO2 composites.
Figure 3. Effect of ZrO2 addition on the porosity of the Al2O3-ZrO2 composites.
found 97.2% of the theoretical density whereas the density increased to 99.2% of the theoretical density in case of 20 vol% ZrO2 addition. The percentage of porosity is 2.8% for pure alumina but for the addition of 20 vol% ZrO2 in alumina matrix, it reduced to 0.8% due to removal of pores from the composites. That means, highly dense and less porous structured was formed when 20 vol% of ZrO2 was incorporated in alumina matrix which could be sintered at 1580˚C for 2 hours. This density and porosity values conform to some previous research works that has been done by pressureless sintering techniques  . Generally, it is well known that, the highest denser and the lowest porous composites provide better mechanical properties. Density also depends on the tetragonal phase retention of ZrO2 in strong alumina matrix around, as the volume of tetragonal phase is lower (~5%) than the monoclinic phase of ZrO2. So, less the t-ZrO2 phase content results the highest densification of the composites. It is observed from XRD data that, composite containing 20 vol% of ZrO2 provides the lowest (10.4%) content oft-ZrO2 phases whereas the highest (~70%) t-ZrO2 phases was found for the content of 5 vol% ZrO2. From the grain size analysis of sintered sample, it was found that, initially the grain size of Al2O3 decreased significantly with increasing vol% of ZrO2 content and further addition led to decrease the grain size slowly. Finer grain size is more expected for the homogeneous distribution of the particles results in the increase in density. So, grain size of Al2O3 matrix was found minimum for 20 vol% ZrO2 content into it and maximum for pure Al2O3.
4.2. Vickers Microhardness (Hv) and Elastic Modulus (E)
Vickers microhardness of sintered studied materials as a function of vol% of zirconia is shown in Figure 4. This property may be described on the basis of porosity and grain size.
Figure 4. Effect of ZrO2 content on hardness of the Alumina-Zirconia composites.
From the Figure 4, it is observed that, the hardness of the ZTA composite decreases (17.2 to 12.98 GPa) with the addition of zirconia though initially it is increased (17.35 GPa) slightly with zirconia content up to 5 vol%. As zirconia has lower hardness than the alumina. So, there will be general tendency of decreasing in hardness with increasing zirconia content. From the SEM analysis it was observed that grain size of alumina decreased with the addition of zirconia but this rate was very significant in case of lower content of zirconia up to 5 vol% after that it was almost linear. On the other hand, the grain size of zirconia is increased (0.35 - 0.48 μm) from lower to higher amount of addition into the alumina matrix. Due to the coarsening of zirconia grains and the formation of subsequent porosity in the ZTA composite, the hardness of the sintered materials will be decreased with higher amount of zirconia. But for 5 vol% ZrO2, the lower content of zirconia (hardness also lower than alumina) and abrupt grain size decreased of alumina results the maximum hardness (17.35 GPa) of the studied materials. It has been noticed that, the average grain size has significant impact on microhardness value.
Elastic modulus of the sintered ZTA samples at different concentration of zirconia is represented in Figure 5. Elastic modulus of the composite depends on the volume fraction of the components present in it and their individual modulus of elasticities . As alumina has a higher modulus of elasticity (347.58 GPa) than zirconia (199 ± 2 GPa) . So, the sample containing 2 vol% ZrO2 has the maximum modulus of elasticity (350.1 GPa) and minimum modulus of elasticity (330.56 GPa) for the sample containing the highest amount of zirconia (20 vol% of ZrO2). The increase of the grain size of zirconia and decrease of the grain size of alumina also contributes the lowering of elastic modulus of ZTA composites.
4.3. Flexural Strength and Fracture Toughness
It has been shown from Figure 6 and Figure 7 that, the flexural strength as well as fracture toughness of composite increases linearly with increase of zirconia addition up to 10 vol%, then decreased. This is due to the grain size of zirconia increases linearly with increasing zirconia content. An increase in grain size improves the possibilities of phase transformation (tetragonal to monoclinic), as a result increasing strength and toughness. For pure alumina maximum flexural strength was obtained 425.23 MPa and maximum fracture toughness was obtained 3.95 MPam½. For composite containing unstabilised zirconia maximum flexural strength (495.8 MPa) and maximum fracture toughness (8.54 MPam½)
Figure 5. Effect of ZrO2 content on elastic modulus of the Alumina-Zirconia composites.
Figure 6. Effect of ZrO2 content on flexural strength of the Alumina-Zirconia composites.
Figure 7. Effect of ZrO2 content on fracture toughness of the Alumina-Zirconia composites.
was obtained for composite containing 10 vol% of ZrO2. Improvement of mechanical properties of theZTA ceramics can be explained by t ® m phase transformation of zirconia. This phase change increases the volume of the particle by about 3% - 4% and produces compressive stress in the alumina matrix and act as energy barrier to further growth of any crack. The phase transformation phenomenon can be explained by X-ray diffraction of the sintered specimens (Figure 12). It is found that, the monoclinic phase (m-ZrO2) increases with the addition of ZrO2 at the same time t-ZrO2 retention decreases. Up to 10 vol% ZrO2 addition t-ZrO2 retention is obtained 70 - 80 vol% but for 15 vol% and 20 vol% ZrO2 addition t-ZrO2 retention decreased significantly (20 - 40 vol%). So, due to presence of large portion of m-ZrO2 and small portion of t-ZrO2, the flexural strength and fracture toughness of ZTA composites containing above 10 vol% unstabilised ZrO2 is decreased.
4.4. X-Ray Diffraction (XRD) Analysis
4.4.1. Phase Analysis of Raw Materials
The XRD patterns of the raw materials (alumina and unstabilised zirconia) for Alumina-Zirconia composites are presented in Figure 8 and Figure 9 respectively. These patterns confirm their corresponding phases’ availability.
Figure 8 shows the XRD pattern of raw alumina which confirms the presence of α-alumina (corundum) by ICDD 00-089-7717. α-Alumina is the most stable crystalline form of alumina containing rhombohedral structure. Three major characteristic peaks were obtained from the planes (104), (113) and (116) at 2θ values are 35.11˚, 43.32˚ and 57.48˚, respectively. The crystallite size of alumina was obtained 23.39 nm.
Figure 9 shows the XRD pattern of raw unstabilised zirconia which confirms the presence of monoclinic zirconia (baddeleyite) by ICDD 00-037-1484. Three
Figure 8. XRD pattern of raw alumina.
Figure 9. XRD pattern of raw unstabilised Zirconia.
main characteristics peaks were obtained from the planes (−111), (111) and (022) at 2θ values are 28.14˚, 31.41˚ and 50.10˚, respectively. Generally, zirconia remains in monoclinic phase at room temperature. This phase is stable up to 1170˚C. Above 1170˚C monoclinic zirconia transforms to tetragonal zirconia and then to cubic phase at 2370˚C.
4.4.2. Phase Analysis of Sintered Sample
The XRD patterns of sintered pure alumina and ZTA composite containing 10 vol% of unstabilised zirconia sintered at 1580˚C for 2 hours are shown in Figure 10 and Figure 11 respectively which exhibits the content of different phases.
Figure 10 shows the XRD pattern of alumina disc sintered at 1580˚C. As like as raw alumina the phase was identified by ICDD 00-089-7717 as α-alumina (corundum). Three major characteristic peaks were obtained at 2θ values 35.14˚, 43.36˚ and 57.51˚ which are almost similar to that of the raw alumina. But the peak intensity is significantly higher than the raw alumina’s peak intensity. The crystallite size of alumina obtained was 32.48 nm which is also larger than that of raw alumina.
Figure 10. XRD pattern of sintered pure alumina (Ts = 1580˚C).
Figure 11. XRD pattern of the sintered ZTA composite containing 10 vol% unstabilised zirconia (Ts = 1580˚C).
Figure 11 shows XRD pattern of ZTA composite containing 10 vol% unstabilised zirconia sintered at 1580˚C which confirms the formation of multi-phase composite. Phases of α-alumina (corundum), monoclinic zirconia (m-ZrO2) and tetragonal zirconia (t-ZrO2) were identified by ICDD 00-089-7717, ICDD 00-037-1484 and ICDD 01-072-7115 respectively. At high temperature m-ZrO2 transforms into tetragonal phase (t-ZrO2) but during cooling some of the ZrO2 phase remains in tetragonal form rather than monoclinic phase due to presence of strong alumina matrix around. The improvement in strength and toughness of Alumina-Zirconia composite results from the volume expansion and shear strain arising from tetragonal to monoclinic phase transformation of ZrO2. Each tetragonal particle release energy and expand to stable size in monoclinic form if a crack tries to propagate under stress.
4.4.3. Variation of XRD Pattern with Zirconia Content
The XRD patterns of ZTA ceramics containing 2, 5, 10, 15 and 20 vol% unstabilised ZrO2 sintered at 1580˚C for 2 hours are shown in Figure 12, which demonstrates the content of the different phases.
Figure 12. XRD patterns of ZTA composite containing 2 - 20 vol% of unstabilised ZrO2 (Ts = 1580˚C).
Phases of α-alumina (ICDD 00-089-7717)), monoclinic zirconia (00-037-1484) and tetragonal zirconia (ICDD 01-072-7115) were identified for all composites by XRD analysis. It is observed that though m-ZrO2 was used for composite preparation a significant content of t-ZrO2 peaks were found. The intensity of t-ZrO2 initially increased with unstabilised zirconia content. Maximum peak intensity of t-ZrO2 was obtained for composite containing 10 vol% zirconia. Above 10 vol% zirconia peak intensity of t-ZrO2 decreased and minimum intensity was obtained from composites containing 20 vol% zirconia. But intensity of m-ZrO2 continuously increased with zirconia content. Low content of ZrO2 and high percentage of Al2O3 is favorable to retain t-ZrO2 due to the presence of more alumina matrix. As sufficient alumina was available to retain the ZrO2 in tetragonal form, the intensity of t-ZrO2 increased up to the 10 vol% zirconia addition. Above 10 vol% zirconia addition, sufficient amount of alumina was not available to retain the ZrO2 in tetragonal form. As a result, intensity of t-ZrO2 decreased with above 10 vol% zirconia addition. But the intensity of m-ZrO2 increased continuously. Mixture of both tetragonal and monoclinic ZrO2 phases imparts to increase strength and toughness of the ZTA ceramics. The extent of toughening achieved in the composites depend on the particle size of Al2O3 and ZrO2, volume fraction of ZrO2 retained in the metastable tetragonal phase as well as on the relative distribution of Al2O3 and ZrO2 in the matrix . Finer particle size of both Al2O3 and ZrO2 will not only enhance the uniform distribution of Al2O3 and ZrO2 particles, but also increases the possibility of ZrO2 being retained as metastable tetragonal phase .
4.4.4. t-ZrO2 Retention
In the present study, ZTA ceramic composite was fabricated using unstabilizedZrO2 with small amount of sintering aid. It is noticed from the Figure 12 that, theZrO2 particles are mainly of tetragonal phase embedded in corundum (α-Al2O3). The main peaks oft-ZrO2 are sharp and high. From Figure 13 it has been shown that, the t-ZrO2 phase retention is almost 79% for the composite containing 5 vol% ZrO2 which exhibits their good stability. However, the t-ZrO2 fraction decreases and m-ZrO2 phase increases with increasing ZrO2 content and it reduced to 10.4% for the composite containing 20 vol% ZrO2. It is confirmed that, tetragonal phase retained at room temperature as a metastable phase due to presence of hard alumina matrix around, and this phase plays the principal role for the improvement of fracture toughness by transformation toughening mechanism.
Previous research work shows that, fraction of tetragonal phase increases when the quantity of ZrO2 decreases in the composite material (30 vol% of tetragonal phase for 5 vol% ZrO2, but only 5% of tetragonal phase for 20 vol% of ZrO2)  . If the tetragonal phase is overstabilized, the stress required for transformation in the high stress region around a crack tip may be higher than the fracture stress. As a result, the flexural strength of the composite will become low. In this study, ZTA composite consists of a mixture of tetragonal and monoclinic zirconia where tetragonal phase is not overstabilized.
4.5. Scanning Electron Microscopic (SEM) Analysis
Figures 14(a)-(c) show the SEM micrographs of sintered pure alumina and ZTA ceramic composites. Figure 14(a) showed the dark large grain size of alumina and Figure 14(b) and Figure 14(c) showed that, comparatively dark (gray contrast) and large grains are Al2O3 whereas bright (white contrast) and small grains are ZrO2. Both Al2O3 and ZrO2 grains are fairly homogeneous in each composition and ZrO2 grains are distributed throughout the alumina matrix.
Figure 13. Retention of ZrO2 as a function of Zirconia content.
Figure 14. (a) Microstructure of sintered pure aluminadisc; (b) Microstructure of ZTA composite containing 90% Al2O3 and 10% unstabilised ZrO2; (c) Microstructure of AZ composite containing 80% Al2O3 and 20% unstabilised ZrO2.
The addition of ZrO2 creates a pinning effect around the alumina grain and hindered the grain growth of alumina during sintering, even for the lowest zirconia content. The addition up to 10 vol% ZrO2 prevents grain growth of alumina without formation of ZrO2 agglomeration. But in case of 20 vol% of ZrO2 content, the premature agglomeration of ZrO2 was observed in the composite. Figure 14(b) and Figure 14(c) show that the increase in ZrO2 content increases ZrO2 grain and decreases the grain size of alumina.
The present study also shows that, ZrO2 grains are located at the grain boundaries (triple points) of alumina. This occupation of the triple points is increased from lower to higher content of ZrO2 and almost fully occupied for more than 10 vol% ZrO2 content. This result conforms the result that was published in previously .
4.6. Grain Size Analysis
From Figure 15 it is observed that grain size of Al2O3 decreased significantly when a small amount of ZrO2 (5 vol%) is added with alumina. Further addition of ZrO2 led to decrease in alumina grain size slowly and linearly. In the present work maximum average grain size was obtained 6.25 µm for pure alumina. For 5
Figure 15. Effect of ZrO2 content on grain size of alumina in ZTA composites.
Figure 16. Effect of ZrO2 content on Zirconia grain size in ZTA composites.
vol% of zirconia addition alumina grain size decreased to 2.58 µm. Minimum grain size of alumina was obtained 1.34 µm for Alumina-Zirconia composite containing 20 vol% of zirconia. On the other hand, grain size of zirconia in Alumina-Zirconia composite increased linearly with zirconia content (Figure 16). In the present study minimum and maximum grain size of zirconia was obtained 0.35 µm and 0.48 µm for ZTA composite containing 5 vol% and 20 vol% ZrO2 respectively. The present results are harmonious with some previous research . The increase in density of Alumina-Zirconia composite may due to the enhanced compaction with zirconia addition as well as the role of zirconia as a grain refiner to reducing the grain size of alumina.
ZTA composites containing 0 - 20 vol% unstabilized zirconia have been fabricated and 99.2% densification can be achieved at 1580˚C. Homogeneous zirconia particles were dispersed in the alumina matrix and abnormal grain growth of the matrix was not observed. For better mechanical properties, the optimum amount of ZrO2 was found to be 10 vol%. The flexural strength and fracture toughness increase up to this amount of ZrO2 addition. Microhardness and elastic modulus follow the inverse relationship with ZrO2 content. Maximum microhardness (17.35 GPa) and elastic modulus were found for the composite containing 5 vol% and 2 vol% of ZrO2 respectively. Further addition of ZrO2 can degrade the mechanical properties due to grain coarsening. The size of the alumina and intergranular zirconia grains predominantly influences the properties of the ceramic composites. It is hoped that the present study will guide further experimental work in Alumina-Zirconia system, especially for unstabilized zirconia performance.
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