# Increasing Bending Strength of Porcelain Stoneware via Pseudoboehmite Additions

Authors: Omar Aguilar-García; Rafael Lara-Hernández; Azucena Arellano-Lara; José L. Gil-Vázquez; Jaime Aguilar-García
Journal: Journal of Ceramics
 (2014)

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## Abstract

Pseudoboehmite nanoparticles synthesized through the desulfation of Al2(SO4)3 were used to investigate the reinforcement of commercial porcelain stoneware. Fractured specimens investigated by SEM suggest that the added pseudoboehmite precursor generated a nanometric primary mullite phase dispersed in the porcelain glassy phase that limited and stopped the intergranular crack propagation. The porcelain modulus of rupture increased twice the value of the modulus of rupture (108 MPa) as compared with that samples without pseudoboehmite additions. Pseudoboehmite also led to increased densification of porcelain stoneware bodies up to 1250°C as shown by thermodilatometry data.


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## Body

## 1. Introduction

A high volume of porcelain stoneware factories installed around the world have a typical 40–50 wt% kaolinitic clay, 35–45 wt% feldspar, and 10–15 wt% quartz sand composition. Such material is characterized by its high technological properties, like low water absorption (<0.5%) and high bending strength (>35 MPa). After firing, porcelain stoneware shows a typical matrix that consisted of mullite crystals embedded in the glassy phase that holds the coarse quartz particles. Mullitization, a controversial issue, has been studied in the literature for diverse ceramic systems with a view to strengthen the ceramic body. In fact, Zoellner’s [1] theory on the strength of porcelain defines the nature of the mullite as a key phase responsible for the mechanical strength. It appears that generating the correct amount of properly sized mullite is vital in achieving the desired strength. Furthermore, the dispersion-strengthening hypothesis of porcelains proposes that the dispersed particles limit the size of Griffith flaws, leading to increased strength [2]. Strength is a function of the volume fraction of the dispersed phase at low volume fractions, while at high volume fractions the strength is dependent on both the volume fraction and the particle size of the dispersed phase. It has also been extensively reported in the literature [3] that the improvement in mechanical strength of porcelains arises from a prestressing effect whereby the quartz is under the tensile stress, and consequently, the glassy matrix surrounding the quartz grains is under a compressive stress.Primary mullite first occurs as derived from kaolinite reaction series in porcelain compositions heated to around 1000°C. Secondary mullite appears at higher temperature after molten feldspar dissolves clayey phases. In some porcelain systems, tertiary mullite has also been reported [1] as a result of a solution precipitation process from an alumina rich phase. Kaolin and gibbsite as well as synthetic mullite were added by Zanelli et al. [4] to porcelain stoneware to enhance mechanical properties. They found that though the mullite content in the porcelain body increased significantly, the physical and technological properties did not always increase proportional to the mullite content. Boehmite can be a source of nanosized alumina and presumably will make porcelain more reactive and strong in both green and fired states. The influence of boehmite gel additions on the green and sintered properties of alumina porcelain systems was investigated by Belnou et al. [5]. They found that boehmite gel additions increased both bending strength and thermal shock resistance of quartz-free porcelain by shifting the size of residual pores towards lower diameters and enhancing mullitization. Pseudoboehmite may be used in a porcelain paste in order to enhance the mechanical properties that may be expected from the increase in mullite content. A source for mullite in porcelain may come from the dissolution of alumina or alumina precursors saturating the porcelain glassy phase. The dissolution of alumina in alkali silicate glasses (Na2O and K2O) has been studied in the literature [6] by measuring the reduction of the magnitude of the enthalpy of mixing alkali silicates with alumina addition and has been attributed to the reduction of the glass nonbridging oxygen content. The aim of the present work was to study the role of the mullite phase on the mechanical properties of commercial porcelain stoneware and analyzing the resulting microstructure after systematically adding 2, 5, and 10 wt% pseudoboehmite.


## 2. Experimental Procedure

Raw materials used included nepheline syenite (48 wt%), kaolin (30 wt%), ball clay (10 wt%), and quartz sand (12 wt%). The pseudoboehmite was obtained using the U. G. process of the alunite [7]. This process is associated with the alkaline desulfation of the basic compounds [8]. Also, this compound can been obtained with the desulfation of the Al2(SO4)3 using an ammonia solution. The obtained pseudoboehmite has a chemical composition of Al4O3(OH)6. Furthermore, the compound was derived from the commercial sulphate with a chemical composition (wt%) given by Al2O3 (98.9010), SiO2 (0.5560), CaO (0.4960), Fe2O3 (0.0259), ZnO (0.0061), CuO (0.0053), SO3 (0.0048), NiO (0.0032), and K2O (0.0015) [9]. The powders were oven-dried at 100°C for 24 h., and this material was ball-milled to pass a 200 mesh sieve and finally added to the slurry of porcelain by the 2, 5, and 10 wt%. Specimens were formed by slip casting at 69 wt% solids loading, adjusting dispersion conditions by the use of Darvan 7, Darvan 811, and sodium silicate deflocculants [10]. Disc specimens with dimensions of 100 × 10 mm were cast from properly aged slips and dried up at 110°C for 24 h. Firing was done by an electric furnace up to 1250°C, 10°C/min heating rate and 2 h soaking time. Bulk density was determined by water immersion procedures based on ASTM C20. Fired specimens polished and HF etched were characterized by SEM using a JEOL JSM-6300 and X-ray diffraction by a Siemens 400, CuKα 30 kV 25 mA.The hardness (H) and the fracture toughness (KIC) were measured (Mitutoyo MVK-E3 tester) by Vickers indentation on the polished surfaces of the sintered samples (diamond pastes of 6, 3, and 1 μm). Vickers microhardness measurements HV0.2 were made by ISO 6507 using indentation load of 1.961 N [11], and a series of ten measurements were performed to made the statistical analysis. For fracture toughness, the samples were submitted to 10 loads of 9.8 N for 15 s on each indentation. The cracks were measured using the microscope attachment on the microhardness tester immediately after indentation. Crack measurements were only made on indents that were well defined without chipping and for which the cracks did not terminate at pores. The indentation fracture toughness of the material was evaluated selecting a model included by the Palmqvist crack system [11].The Young’s modulus of the samples was measured ultrasonically using an impulse-excitation of vibration technique (Grindo-Sonic, J. W. Lemmens Inc.) according to ASTM standards C 1259-94. This method covers a dynamic determination of the elastic properties of materials at ambient temperature. Young’s modulus was computed using the resonant frequency in the flexural and torsion modes of vibration. The bending strength of fired test bars was measured under a three-point bending test by a universal instron machine model 3366 according to ASTM 1161-90. The final results were taken of the average of four replications for Young’s modulus, the bending strength, and the physical properties.


## 3. Results and Discussion

The synthesized pseudoboehmite with a (Al4O3(OH)6 composition that consisted of nanometric whiskers is known to undergo several structural thermal transformations including the γ-alumina formation at 500°C; however, at porcelain vitrification temperatures, it is expected to dissolve in the glass and contribute to mullite formation. Figure 1 shows shrinkage behavior of porcelain samples with increasing pseudoboehmite additions. It is seen that such additions increase the shrinkage level within the whole range of densification, implying a drastic reduction in porosity, particularly from 1100°C to 1160°C with obvious implications on strengthening. This is in agreement with the work of Belnou et al. [5] who found that pseudoboehmite additions in alumina porcelain shifted the size of residual pores towards lower diameters. It is also seen by Figure 1 that the rate of shrinkage in pseudoboehmite (PB) added samples becomes more gradual which may reduce faults and defects brought about by sudden structural rearrangements within the body.Figure 1
Thermodilatometry data showing higher shrinkage within the whole range of densification as pseudoboehmite additions increase.The dilatometric curves of the compositions have been studied (Figure2). The composition with 0 wt% of PB shows a typical behavior of the porcelain stoneware. As it can be noticed at 510–570°C, as a result of the kaolinite dehydration and metakaolinite formation, some shrinkage is observed, followed by a volume increase at ~580°C, due to the transformation of α-quartz to β-quartz. The compositions show considerable shrinkage at ~1000°C. The shrinkage may be associated with the liquid development, mullitization, and densification. As pseudoboehmite is added, implying lower mullitization temperature was brought about by the highly reactive pseudoboehmite sol dissolved in the glass. It therefore appears that pseudoboehmite additions may ease mullite formation.TDD curves corresponding to TD curves shown in Figure1.
(a)
(b)
(c)
(d)The derived dilatometric curves have been prepared (Figure3). These curves show the differences between the compositions. As PB is added, decomposition of clays occurs at lower temperatures. Around 1045°C, a peak is observed in the sample without additions of PB; this change is associated with the nucleation of primary mullite from metakaolinite. As PB is added, it can be seen that peak appears at a lower temperature. Samples with additions of 5 wt% and 10 wt% of PB, the third peak appears associated with the formation of secondary mullite, attributable to the high reactivity of PB particles with the liquid phase. The importance of these curves is that the position of their minimums values indicates the reactivity of the various compositions. The sequence of reactivity by increasing temperatures is 10% > 5% > 2% > 0%. The reactivity of the composition is due to the corresponding additions of PB.Figure 3
X-ray diffraction patterns of experimental porcelain compositions fired at 1200°C for boehmite additions (2, 5, 10 wt%). *Note moderate increase in the mullite peaks intensity.This assumption was confirmed by the XRD results of samples, sintered at 1200°C (Figure3). Mullite phase increases moderately with added pseudoboehmite as shown in Figure 3 by X ray diffraction. The aspect ratio of the acicular mullite also increases with both pseudoboehmite additions and temperature as shown by SEM in Figure 4. In general it is seen that mullite needles coarsen, leading to a smaller number of larger needles. Figure 5 shows a fracture surface in a 10 wt% pseudoboehmite sintered at 1150°C specimen where an intergranular type of crack that propagates among primary mullite is being stopped by a cluster of nanometric mullite (2/3 Al2O3/SiO2) crystals as determined by EDX.SEM micrographs of etched surfaces showing acicular mullite formation. Note increasing aspect ratio of mullite needles depending on both temperature (left to right) and composition (top to bottom).
(a)
(b)
(c)
(d)SEM micrographs porcelain stoneware fracture surfaces. (a) A crack stops at a spot of high mullite concentration. (b) Intergranular crack propagates among primary nanometric mullite (2/3 Al203/Si02) crystals.
(a)
(b)The statistical treatment of physical and mechanical measurements has enabled the elaboration of mathematical models and permitted not only to simulate the mechanical behavior, but also to evaluate the contribution of the various experimental parameters involved in. By ANOVA analysis, the factors with statistical relevance have been defined, while by least squares method their coefficients in the mathematical model have been calculated. Table1 lists average values of measured physical and mechanical properties obtained for three replications. The results of experiments designed in Table 1 were analyzed using ANOVA method and the results are in Tables 2 and 3. Based on the data of Table 2, the pseudoboehmite and the temperature have statistical significance, the significance of the factors were obtained by comparing theF calculated value versus theF tabulated value in the Fisher-Snedecor distribution; if theF calculated values are higher than theF tabulated values (at the required level of significance) is considered to exist statistical significance, all theF values presented in Table 2 are higher than the tabulated. Both the temperature and the additions of PB have a positive effect on the bulk density and porosity. This is consistent with the stated above in dilatometric curves, where it was observed that the formation of glassy phase was obtained at higher temperatures and additions of PB, enabling that the liquid phase can surround the clay relicts and quartz, and the achieving of a higher density. Increased porosity was consistent with the published results for Belnau et al. [5], limiting PB additions to the mixture of porcelain.Table 1
Experimental physical and mechanical properties.
Pseudoboehmite addition (wt%)
Firing Temp. (°C)
Sample
Modulus of rupture (MPa)
Bulk density (g/cm3)
Young’s modulus (GPa)
Vickers microhardness (GPa)
Fracturetoughness
KIC (MPa·m1/2)
Porosity(%)
2
115012001250
147
9256.942.7
2.12.01.9
49.557.564.34
6.17.06.8
1.41.61.7
5.66.67.6
5
115012001250
258
81.294.5107.4
2.22.22.1
40.560.262.2
6.86.86.9
1.51.71.5
5.17.87.5
10
115012001250
369
76.370.2101.8
2.02.12.0
32.85356.8
6.47.16.4
1.21.51.5
7.99.412.6
M.Dondi et al. [12]
1200
50
2.4-2.5
79
6.5
1.2
Zanelli et al. [4]
1220
42
2.2–2.4
1.1
4–12.8Table 2
Analysis of variance of bulk Density and porosity.
Bulk density
Porosity
Factor
SS
df
MS
F
P
Factor
SS
df
MS
F
P
TemperatureL + Q
0.02
2.00
0.01
5.87
0.06
TemperatureL + Q
13.88
2.00
6.94
7.05
0.05
PB (%)L + Q
0.05
2.00
0.02
11.34
0.02
PB (%)L + Q
21.74
2.00
10.87
11.04
0.02
Error
0.01
4.00
0.00
Error
3.94
4.00
0.98
Total
0.08
8.00
Total
39.55
8.00Table 3
Analysis of variance of Young’s modulus and Vickers microhardness.
Young’s modulus
Vickers microhardness
Factor
SS
df
MS
F
P
Factor
SS
df
MS
F
P
TemperatureL + Q
679.92
2.00
339.96
26.71
0.00
TemperatureL + Q
0.34
2.00
0.17
1.58
0.31
PB (%)L + Q
145.48
2.00
72.74
5.72
0.07
PB (%)L + Q
0.09
2.00
0.04
0.42
0.69
Error
50.90
4.00
12.73
Error
0.43
4.00
0.11
Total
876.30
8.00
Total
0.86
8.00Table3 shows that the independent variables have a statistical significance for the Young’s modulus, but for the Vickers microhardness they do not have a statistical significance. The temperature and the additions of PB have a positive effect on Young’s modulus. At higher temperature and additions of PB, the properties of modulus of elasticity increase (Figure 6). For Vickers microhardness, temperature and PB additions have no significant effect; this has important implications for improving the mechanical properties since it does not want to make more fragile materials. The modulus of rupture varies with both temperature and pseudoboehmite additions. The highest modulus (108 MPa) occurs for the 5% and 10% of pseudoboehmite additions, which is an important increase in strength as compared to samples without pseudoboehmite additions and those reported in the literature [12] that present about half of the latter value (50 Mpa). Regarding the effect of the temperature on the modulus of rupture, the higher modulus measurements (108 and 102 MPa) correspond to samples with higher levels of pseudoboehmite (5 and 10 wt%) heated up to 1250°C. On the contrary specimens that contain 2% pseudoboehmite and therefore less refractoriness present low strength (43 MPa) at the same temperature (1250°C). This entire phenomenon can be observed in Figures 6 and 7. Fracture toughness in pseudoboehmite containing samples almost doubles the value 1.2 presented by pseudoboehmite free specimens as shown in Table 1. The fracture toughness showed some variation both with sintering temperature and pseudoboehmite additions as shown in Figure 8. The highest value of K1C was obtained with 5% PB and sintering at 1200°C, and this is a consequence of the quantity of crystalline phase and lower porosity, limiting the propagation of Griffith cracks.Figure 6
3D surface response of Young’s modulus versus pseudoboehmite additions and temperature.Figure 7
3D surface response of modulus of rupture versus pseudoboehmite additions and temperature.Figure 8
3D surface response of fracture toughness versus pseudoboehmite additions and temperature.By analyzing the three graphs of surface, it can be seen that the higher areas are reached at a temperature of 1200°C and 5% PB additions. The combination of these factors achieves a synergistic effect between the amount of liquid present and PB particles, and this is a consequence of the highest density of the sample, the decrease in the porosity, and the extra mullitization promoted by the additions of PB that creates a barrier that stops the cracks.


## 4. Conclusions

The high reactivity of pseudoboehmite sol additions presumably increased the amount of alumina dissolved in the glass, thereby increasing moderately the precipitated mullite phase content. It appears that strengthening of the porcelain may be caused by a dispersion-strengthening mechanism rather than by a substantial increase in the mullite phase content. Primary mullite nanometric crystal clusters were shown to limit the intergranular crack propagation, in agreement with the dispersion-strengthening hypothesis whereby dispersed particles limit the size of Griffith flaws leading to increased strength. Also, pseudoboehmite additions allowed the reinforcement of green bodies producing less body defects and higher densification.



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*Source: 270689-2014-04-28.xml*