# Impact of Blending on Strength Distribution of Ambient Cured Metakaolin and Palm Oil Fuel Ash Based Geopolymer Mortar

Authors: Taliat Ola Yusuf; Mohammad Ismail; Jamilu Usman; Ainul H. Noruzman
Journal: Advances in Civil Engineering
 (2014)

---

## Abstract

This paper investigates the influence of blending of metakaolin with silica rich palm oil fuel ash (POFA) on the strength distribution of geopolymer mortar. The broadness of strength distribution of quasi-brittle to brittle materials depends strongly on the existence of flaws such as voids, microcracks, and impurities in the material. Blending of materials containing alumina and silica with the objective of improving the performance of geopolymer makes comprehensive characterization necessary. The Weibull distribution is used to study the strength distribution and the reliability of geopolymer mortar specimens prepared from 100% metakaolin, 50% and 70% palm and cured under ambient condition. Mortar prisms and cubes were used to test the materials in flexure and compression, respectively, at 28 days and the results were analyzed using Weibull distribution. In flexure, Weibull modulus increased with POFA replacement, indicating reduced broadness of strength distribution from an increased homogeneity of the material. Modulus, however, decreased with increase in replacement of POFA in the specimens tested under compression. It is concluded that Weibull distribution is suitable for analyses of the blended geopolymer system. While porous microstructure is mainly responsible for flexural failure, heterogeneity of reaction relics is responsible for the compression failure.


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## Body

## 1. Introduction

Concrete made from Portland cement is described as quasi-brittle with features strongly influenced by mechanical and chemical behavior of micro- to mesostructures when subjected to stresses [1]. The fracture behavior is thus affected by the existence of microdefects in the form of microcracks, voids, and weak heterogeneous zones in the material [1–3]. Consideration of hardened concrete fracture behavior is therefore paramount in structural safety assessment [4]. The random nature of cracks or flaws brings about scatter in strength and therefore lends support for statistical consideration. Normal distribution has been commonly used to describe the strength behavior of concrete materials. The use of the normal distribution is appealing because of its simplicity. However, it is limited by parameter prescription of scale factor extending to negative values even though the strength at fracture of a material cannot take on values less than zero [5]. Furthermore, the chance of obtaining the crack size greater than critical crack increases with volume of test specimens and this volume dependency is responsible for a decrease in the mean strength as the volume of specimen increases bringing about invariant problem with respect to parameters of normal distribution [6, 7]. The lack of theoretical basis for the application of normal distribution sets it against other distributions with deep theoretical considerations [8]. A rational basis is the characterization of material strength based on extreme value distributions because a material fails by the weakest link manifested by the largest flaw in the material. The distribution of sample tests, for instance, is skewed to follow the tail of population distribution necessitating focus on extreme values at tail to yield parametric functions applied in extreme value statistical models [9]. Gumbel, Frechet, and Weibull distributions are examples of extreme value distributions. However, the Weibull distribution is favored because of its bounds that limit the lowest fracture strength to zero and the flexibility of the shape parameter; a relatively small number of test specimens can provide reasonably accurate estimates of failures and it provides graphical plots very useful for result analysis [9]. Brittle materials like ceramics are commonly characterized using Weibull distribution function [6, 10] because the statistics of the mechanical and failure properties adequately fit into the Weibull distribution [11]. ASTM C1239 [12] provides detail procedures for implementation of Weibull distribution in structural designs using ceramics. Studies have also reported the use of Weibull distribution to successfully describe the strength data of ordinary Portland cement concrete [8, 13]. It was reported that the Weibull distribution gave the best result for concrete mechanical properties when compared to normal and log normal distributions [14].Geopolymer as cementitious material prepared from activation of aluminosilicate such as fly ash and metakaolin with alkaline solution from sodium/potassium hydroxide and silicate has evolved as alternative to Portland base cementitious material such as mortar and concrete. Oven cured fly ash based geopolymer concrete was found to behave in a more brittle manner than the conventional Portland cement based concrete [15]. It has also been reported that fly ash based geopolymer concrete and paste have less characteristic fracture length than those of the ordinary Portland cement concrete, accompanied by a decrease in fracture energy and modulus of elasticity and increase in tensile splitting strength of the geopolymer concrete indicating a higher brittleness of the geopolymer [16]. It was further reported that matrix of formation of fly ash geopolymer and OPC concrete through geopolymerization and hydration reactions, respectively, is responsible for the difference in their behavior [16]. This should be expected because geopolymer, an X-ray amorphous inorganic polymeric material, falls within the broad group of ceramic materials [17] which are good examples of brittle materials. Geopolymer is a group of cementitious materials formed by activating aluminosilicate based material with alkaline solution containing a mixture of hydroxide and silicate of alkali earth metal (sodium or potassium). The reaction between trivalent aluminum and tetravalent silicon forms long ranged covalent and ionic bond of polymeric networks.Brittleness in ceramics results in wide strength distributions that limit its use in construction. The brittle nature of geopolymer is therefore a motivation for characterization of its strength and distribution. This is specifically needed to understand the behavior of the material which may be influenced by the heterogeneity arising from the use of waste materials as the primary source of aluminosilicate requirements for its synthesis. For instance, the use of metakaolin for geopolymer production is limited by high demand for activating alkali due to relatively low silica/alumina ratio [18]. Also morphology of the particles necessitates excessive water demand to achieve adequate flow; else high shear mixing would have to be used [19, 20]. This may be detrimental to the performance of the geopolymer especially with respect to shrinkage [19] and behavior under exposure to fire [21]. To solve this problem, metakaolin may be blended with silica rich waste materials such as palm oil fuel ash (POFA) that would reduce costs, adjust the silica alumina ratio to reduce alkali demand, and at the same time preserve mechanical and durability properties. The effect of blending on strength statistics is therefore important for a complete characterization of the material. This however is rarely reported in the literature.This paper therefore studied the effect of varying POFA composition on strength distribution of metakaolin based geopolymer cured in ambient condition by application of the Weibull distribution. The characteristic strength can also be determined to give a measure of reliability of the material strength. The significance of this is that geopolymer as an emerging material may further be characterized in terms of strength and reliability and give insight into the implication of blending, especially with waste materials.


## 2. Experimental Program

### 2.1. Materials

Metakaolin obtained from calcined kaolin at 750°C for 4 hours in the furnace was blended with POFA sourced from a palm oil factory in southern Malaysia. POFA was treated by sieving to collect particles passing through 150-micron sieve. This was followed by grinding in Los Angeles abrasion machine for 5 hours to obtain 95% of particle size less than 45 microns. The chemical composition of metakaolin and POFA as determined by X-ray fluorescence (XRF) is contained in Table1. A mixture of sodium silicate and sodium hydroxide was used for the preparation of geopolymer mortar specimens.Table 1
Chemical composition of Metakaolin and POFA.
Material
SiO2
Al2O3
K2O
Fe2O3
CaO
P2O5
MgO
SO3
Cl
TiO
CO2
Metakaolin
54.7
39.9
2.58
1.43
—
—
0.7
—
—
—
0.1
POFA
63.70
3.68
9.15
6.27
5.97
4.26
4.11
1.59
1.59
0.30
0.1


### 2.2. Methods

Geopolymer mortar prisms (40
×
40
×
160 mm) and cubes (50
×
50
×
50 mm) were prepared from metakaolin and POFA as precursor materials to determine the flexural and compressive strength of 20 specimens for each data set at three levels of blends of 100%, 50%, and 30% by weight of metakaolin with 0%, 50%, and 70% weight of POFA, respectively. The twenty specimens for each series were prepared by activating alumina and silica from metakaolin and POFA with alkaline solution made from sodium hydroxide (NaOH) and sodium silicate (Na2SiO3). The mix proportion is presented in Table 2. The specimens were removed from the moulds 24 hours after casting and were kept at ambient temperature of about 27°C for 28 days. The prism specimens were tested in 3-point load configuration to obtain the flexural strength using Inspiron testing machine with a loading rate of 1 KN/s. The compressive strength was obtained from a universal testing machine also at a loading rate of 1 KN/s. Field emission scanning electron microscopy (FESEM) was used to obtain information about the microstructure of the tested samples.Table 2
Mix Design of Geopolymer Mortar.
MixMK : POFA
Agg. [kg/m3]
MK [kg/m3]
POFA [kg/m3]
Na2SiO3 [kg/m3]
NaOH [kg/m3]
Add. water [kg/m3]
Total water content
100 : 0
1680.0
560.00
—
443.20
155.20
2.67
349.59
50 : 50
1680.0
280.00
280.00
308.30
108.00
53.00
294.24
30 : 70
1680.0
168.00
392.00
205.48
72.00
110.00
270.89


### 2.3. Application of Weibull Distribution for Strength Characterization

Weibull distribution like other extreme value distributions is used to characterize occurrences that are dominantly influenced by the weakest link theory. The important assumption is that the failure of a material is measured by the weaker element possessing small strength. This theory forms the basis for reliability of the strength consideration of brittle materials [2]. Weibull three-parameter cumulative probability function is given as
(1)
P
f
=
1
-
exp
⁡
[
-
(
σ
-
σ
u
σ
θ
)
m
]
,
where u is the minimum stress below which the material will not fail and m is shaping parameter called Weibull modulus and is the scale parameter also known as characteristic or reference strength, the value of which depends on the stress pattern, size of specimens [9, 12], material type, and processing [2]. The significance of m as a material property is that it characterizes the brittleness of the material [22]. The Weibull modulus also reveals the characteristics, severity, and distribution of flaws with a low m value implying a broad spectrum of strength distribution resulting from the nonuniform distribution of flaws, a high m value indicative of homogeneity in flaw distribution resulting in a reduced strength distribution [6, 11], and the typical m values for structural ceramics as influenced by processing route lying between 3 and 12 [6].The stress parameteru when set at zero in line with the fact that strength of materials cannot be below this limit yields the two-parameter distribution. However the three-parameter distribution may still be used for strength with a predetermined lower bound from results of proof or screening tests. With u equal to zero, (1) becomes [9]
(2)
P
f
=
1
-
exp
⁡
(
-
(
σ
σ
θ
)
m
)
.
A double natural logarithm of (2) yields
(3)
ln
⁡
(
1
-
P
f
)
=
-
(
σ
σ
θ
)
m
ln
⁡
[
ln
⁡
(
1
1
-
P
f
)
]
=
m
ln
⁡
σ
-
m
ln
⁡
σ
θ
.The probability of fracture P
f of sample is estimated from
(4)
P
f
=
i
-
0.5
N
,
where N is the number of test specimens and i is the datum [12]. Expression in (3) depicts the reliability of the material. In this study, the flexural strength of 20 specimens was ranked in ascending order and the corresponding P
f was calculated using (4) to obtain the left side of(3)Plotting the left side of (3) against ln on the right of strength data and fitting the data points yielded a line with a slope m which is an estimate of the Weibull distribution. Similarly, the characteristic strength was determined by obtaining the value of strength that corresponds to a zero value of ln
⁡
[
ln
⁡
(
1
/
1
-
P
f
)
] or P
f of 63.2%. The curve fitting was performed using linear regression analysis [23].


## 2.1. Materials

Metakaolin obtained from calcined kaolin at 750°C for 4 hours in the furnace was blended with POFA sourced from a palm oil factory in southern Malaysia. POFA was treated by sieving to collect particles passing through 150-micron sieve. This was followed by grinding in Los Angeles abrasion machine for 5 hours to obtain 95% of particle size less than 45 microns. The chemical composition of metakaolin and POFA as determined by X-ray fluorescence (XRF) is contained in Table1. A mixture of sodium silicate and sodium hydroxide was used for the preparation of geopolymer mortar specimens.Table 1
Chemical composition of Metakaolin and POFA.
Material
SiO2
Al2O3
K2O
Fe2O3
CaO
P2O5
MgO
SO3
Cl
TiO
CO2
Metakaolin
54.7
39.9
2.58
1.43
—
—
0.7
—
—
—
0.1
POFA
63.70
3.68
9.15
6.27
5.97
4.26
4.11
1.59
1.59
0.30
0.1


## 2.2. Methods

Geopolymer mortar prisms (40
×
40
×
160 mm) and cubes (50
×
50
×
50 mm) were prepared from metakaolin and POFA as precursor materials to determine the flexural and compressive strength of 20 specimens for each data set at three levels of blends of 100%, 50%, and 30% by weight of metakaolin with 0%, 50%, and 70% weight of POFA, respectively. The twenty specimens for each series were prepared by activating alumina and silica from metakaolin and POFA with alkaline solution made from sodium hydroxide (NaOH) and sodium silicate (Na2SiO3). The mix proportion is presented in Table 2. The specimens were removed from the moulds 24 hours after casting and were kept at ambient temperature of about 27°C for 28 days. The prism specimens were tested in 3-point load configuration to obtain the flexural strength using Inspiron testing machine with a loading rate of 1 KN/s. The compressive strength was obtained from a universal testing machine also at a loading rate of 1 KN/s. Field emission scanning electron microscopy (FESEM) was used to obtain information about the microstructure of the tested samples.Table 2
Mix Design of Geopolymer Mortar.
MixMK : POFA
Agg. [kg/m3]
MK [kg/m3]
POFA [kg/m3]
Na2SiO3 [kg/m3]
NaOH [kg/m3]
Add. water [kg/m3]
Total water content
100 : 0
1680.0
560.00
—
443.20
155.20
2.67
349.59
50 : 50
1680.0
280.00
280.00
308.30
108.00
53.00
294.24
30 : 70
1680.0
168.00
392.00
205.48
72.00
110.00
270.89


## 2.3. Application of Weibull Distribution for Strength Characterization

Weibull distribution like other extreme value distributions is used to characterize occurrences that are dominantly influenced by the weakest link theory. The important assumption is that the failure of a material is measured by the weaker element possessing small strength. This theory forms the basis for reliability of the strength consideration of brittle materials [2]. Weibull three-parameter cumulative probability function is given as
(1)
P
f
=
1
-
exp
⁡
[
-
(
σ
-
σ
u
σ
θ
)
m
]
,
where u is the minimum stress below which the material will not fail and m is shaping parameter called Weibull modulus and is the scale parameter also known as characteristic or reference strength, the value of which depends on the stress pattern, size of specimens [9, 12], material type, and processing [2]. The significance of m as a material property is that it characterizes the brittleness of the material [22]. The Weibull modulus also reveals the characteristics, severity, and distribution of flaws with a low m value implying a broad spectrum of strength distribution resulting from the nonuniform distribution of flaws, a high m value indicative of homogeneity in flaw distribution resulting in a reduced strength distribution [6, 11], and the typical m values for structural ceramics as influenced by processing route lying between 3 and 12 [6].The stress parameteru when set at zero in line with the fact that strength of materials cannot be below this limit yields the two-parameter distribution. However the three-parameter distribution may still be used for strength with a predetermined lower bound from results of proof or screening tests. With u equal to zero, (1) becomes [9]
(2)
P
f
=
1
-
exp
⁡
(
-
(
σ
σ
θ
)
m
)
.
A double natural logarithm of (2) yields
(3)
ln
⁡
(
1
-
P
f
)
=
-
(
σ
σ
θ
)
m
ln
⁡
[
ln
⁡
(
1
1
-
P
f
)
]
=
m
ln
⁡
σ
-
m
ln
⁡
σ
θ
.The probability of fracture P
f of sample is estimated from
(4)
P
f
=
i
-
0.5
N
,
where N is the number of test specimens and i is the datum [12]. Expression in (3) depicts the reliability of the material. In this study, the flexural strength of 20 specimens was ranked in ascending order and the corresponding P
f was calculated using (4) to obtain the left side of(3)Plotting the left side of (3) against ln on the right of strength data and fitting the data points yielded a line with a slope m which is an estimate of the Weibull distribution. Similarly, the characteristic strength was determined by obtaining the value of strength that corresponds to a zero value of ln
⁡
[
ln
⁡
(
1
/
1
-
P
f
)
] or P
f of 63.2%. The curve fitting was performed using linear regression analysis [23].


## 3. Results and Discussion

### 3.1. Effect of POFA Blend on the Stress-Strain Behavior

The flexural stress-strain curves of three specimens at 28 days each from the 20 specimens of 100% metakaolin, 50% POFA, and 70% POFA are illustrated in Figure1. All the three samples show abrupt failure at varying peak stresses with the strains at failure being 0.003, 0.0028, and 0.0024, respectively, and the absence of the plastic range indicating the brittleness of the material. Apart from stress decrease with increase in POFA, blending with POFA does show the influence on brittleness given the reduction in the steepness of the stress-strain curves with increasing POFA. Brittleness is attributed to the existence of high geopolymerization products [24].Figure 1
Influence of POFA on stress-strain behavior geopolymer specimen.


### 3.2. Regression Analysis of Geopolymer Weibull Plots

The linear fitting of experimental data in Figures2 and 3 indicates adequate regression coefficient (R
2) of the plots. The model terms for the different mixes are indicated on the graphs. To further confirm the closeness of the test data with the regression data, analysis of variance (ANOVA) was performed. Only the ANOVA of mix with 100% metakaolin is presented in Table 3. The ANOVA tests confirmed that, at 0.05 levels, the regression data is not significantly different from the test data for all the mixes. Similar results were obtained in all the mixes confirming the adequacy of the Weibull regression models.Table 3
One Way ANOVA of 100% metakaolin geopolymer Weibull regression.
DF
Sum of Squares
Mean Square
F Value
Prob >F
Model
1
1.64034
E
-
6
1.64034
E
-
6
1.073222E − 6
0.9918
Error
38
58.08007
1.52842
Total
39
58.08007
Homogeneity of Variance Test
Model
1
0.00931
0.00931
0.01583
0.90054
Error
38
22.35035
0.58817Figure 2
Weibull graph of flexural strength of blended geopolymer.Figure 3
Weibull graph of compressive strength of blended geopolymer.Tables4 and 5 illustrate the comparison between Weibull and normal distribution parameters. The Weibull characteristic strengths for the mixes are more conservative when compared to those evaluated for normal distribution, for instance, at the usual 0.05 significant levels. From the study of Tumidajski et al. [8] it is not obvious that the Weibull modulus directly depended on the characteristic strength and as such it cannot be concluded here also that obvious relationship exists.Table 4
Comparison of Weibull and Normal Distribution Parameters for Flexural Strength.
Mix
Weibull
Normal
Characteristic Strength (MPa)
Modulus
Mean Strength (MPa)
Standard Deviation
100%  MK
14.35
9.76
13.64
1.69
50% POFA
11.97
11.55
11.45
1.18
70% POFA
9.47
16.59
9.08
0.65Table 5
Comparison of Weibull and Normal Distribution Parameters for Flexural Strength.
Mix
Weibull
Normal
Characteristic Strength (MPa)
Modulus
Mean Strength (MPa)
Standard Deviation
100%  MK
67.40
15.56
67.12
5.22
50% POFA
60.58
14.74
58.41
5.03
70% POFA
48.95
12.37
43.83
4.04


### 3.3. Effect of Blending on Strength Distribution

Using Weibull plots of Figure3 to study the effect of blend on the distribution of the strength, it was observed that, generally, the Weibull modulus for flexural strength increased with replacement of metakaolin by POFA, indicating that flexural strength variability reduces with increase in POFA content. It can be observed in Figure 2 that the slope of the line for the 100% metakaolin geopolymer is 9.763 which is an estimate of Weibull modulus for the set of pure metakaolin specimens. A slope of 11.3 was obtained from specimens with 50% POFA replacement while that for 70% POFA replacement is 16.69 which are in tandem with the brittle behavior of Figure 1. This tends to indicate that the ceramic-like behavior (wide strength distribution) of the geopolymer samples reduces with increase in POFA replacement considering that modulus for ceramics lies between 3 and 12 [6].The microstructure of specimens prepared from 100% metakaolin revealed heterogeneous grain comprising loose structured precipitates forming around the sheetlike packing of unreacted metakaolin with interconnected pores (Figure4(b)). This may be responsible for the broad characteristic strength of the specimen as the sheetlike arrangement with micropores gives way to more homogenous densely packed microstructure with reduced micropores as the POFA replacements in the specimens increased to 50% and 70%. The Si/Al ratio of 100% metakaolin which is less than 3 (Si/Al = 2.41) leads to the formation of geopolymer with stiff and brittle properties as its three-dimensional structure of cross-linked rigid networks [25] fails abruptly in the presence of flaws such as voids (Figure 4(b)). The higher Si/Al ratios of 50% and 70% POFA blended geopolymers (Si/Al = 4.49 and 6.72) tend to form a less rigid structure transiting from a three-dimensional to a two-dimensional network. The wriggles observed in the curves of 50% and 70% POFA (Figure 2) may be attributed to flaws from volume distributed relics of POFA in the microstructure [9]. The pure metakaolin specimen has the lowest Weibull modulus falling in the range of ceramic material (3 to 12). That for 50% POFA replacement barely falls in the range while that for 70% replacement is outside the range of ceramic. The implication of this is that the pure metakaolin system with the lowest Weibull modulus has broad flexural strength distribution and that for 70% has narrow flexural strength distribution with 50% falling in-between. As earlier mentioned, narrow distribution is a feature of a relatively homogeneous distribution of flaws. Material presenting narrow strength distribution is preferable because such a material is more predictable and has the least chance of failure at a stress lower than the characteristic value [9].FESEM of metakaolin powder and geopolymer specimens.
(a)
Metakaolin powder
(b)
100% MK geopolymer
(c)
50% POFA geopolymer
(d)
70% POFA geopolymerThe Weibull modulus for compression strength of 100% metakaolin and 50% and 70% POFA replacement is shown in Figure3. The modulus for geopolymer with 100% metakaolin and 50% and 70% POFA is 15.557, 14.070, and 12.367, respectively. This shows that variability is the highest for geopolymer with 70% POFA and the lowest for that with 100% metakaolin under compression loading.It is interesting to note that while the strength variability increased with POFA replacement in compression test, the opposite is the case for bending strength. Also, Weibull variability trends in compression also differ from that of a normal distribution of Table4. This may be due to the fact that Weibull variability results mainly from flaws in the material structure. Furthermore, fracture in bending is mainly influenced by micropores which are seen to be predominant in the pure metakaolin system (Figure 4(b)) while variability in compressive failure may be due to heterogeneity caused by unreacted POFA which are noticeable in Figures 4(c)and 4(d). The failure mode in compression may be as a result of slow propagation of many cracks that coalesced to create a crushing zone as against the rapid and unstable crack development typical of flexural failure [8]. While the presence of reaction relics may be playing a major role in the crushing failure of specimens, the micropores may be the dominant factor responsible for scatter in flexural failure.


### 3.4. Effect of Blending on Characteristic Strength

The Weibull characteristic flexural strength obtained at 63.2% probability of fracture is the highest with a value of 14.339 MPa for the geopolymer samples prepared with 100% metakaolin (Figure2). Characteristic strength values reduced with increasing POFA replacement to give values of 12.013 MPa and 9.38 MPa for 50% and 70% POFA replacement, respectively. The characteristic flexural strength gives an indication of the fracture toughness of the material as an increase in strength depicts increase in fracture toughness [26]. The higher characteristic strength for pure metakaolin based geopolymer may therefore result in high fracture toughness even though it manifested relatively broad band distribution of brittle materials.In a similar manner, characteristic compressive strength decreased with POFA replacement as indicated in Figure3. The characteristic compressive strengths are 69.4 MPa, 60.58 MPa, and 46.95 MPa for 100% metakaolin and 50% and 70% POFA, respectively.The trend of both characteristic flexural and compressive strengths due to POFA replacement may be as a result of Si/Al ratio of the primary material which plays a major role in the strength of geopolymer. The availability of silica and alumina influences the extent and rate of polymeric reaction. Hypothetically, the strength of the geopolymer should increase with increase in the Si/Al ratio because Si–O–Si bonds, which are stronger than Si–O–Al and Al–O–Al bonds, should be more with increase in Si/Al ratio. This is however usually not the case due to some other synthesis factors [27]. Increase in POFA replacement raises the Si/Al ratio from 2.41 for pure metakaolin geopolymer to 4.49 and 6.72 for 50% and 70% POFA mixes, respectively. The high volume replacement with POFA may prevent complete reaction of the materials leaving behind relics as observed in Figures 4(c) and 4(d). The reduction in strength may therefore be due to the existence of these relics that have not been used in the polymerization process. They form the volume distributed flaws that act as the “weakest link” in the microstructure, thus becoming the major determinant of the fracture strength of the material.


### 3.5. Field Emission Scanning Electron Microscopy

Field emission scanning electron microscopy (FESEM) micrographs of metakaolin starting material are shown in Figure3 and those of geopolymer specimen are shown in Figures 4(a), 4(b), 4(c), and 4(d). The gel formation in the microstructure of the metakaolin geopolymer is shown in Figure 4(b) to be predominantly formed to take after the platy sheets of metakaolin. This arrangement does not allow for complete filling of spaces between the sheets by the gel. The micropores also observed by Hawa et al. [28] vary in volume and size within the entire microstructure. The marked difference in grain direction of the sheets which are irregularly arranged could result in varying the induced microresistance to applied load by different specimen depending on the nature of formed gel laminates and hence the broad distribution of strength at failure observed in flexural loading.The micrograph of 50% POFA specimen in Figure4(c) presents less packed gel laminates that take after the metakaolin particle shapes in the microstructure. The reduced presence of the sheetlike grains suggests a better consistency in the gel formation that may be responsible for the reduced flexural strength variability. However, there exist some artifacts from incomplete reaction of metakaolin rubbing off on the homogeneity of the microstructure. The relics which appeared to be minimally distributed tend to have influence on the variability of compressive strength in a similar manner. Figure 4(d) showing the micrograph of 70% POFA mortar revealed a microstructure with a noticeable presence of POFA relics and absence of the platy grain gel.


### 3.6. X-Ray Diffraction

The XRD patterns of the geopolymer mortar are shown in Figure5. The broad band and low intensity patterns exhibited between 24° and 28° at 2-theta angle for three specimens indicate a high degree of amorphous structure of the mortar which is characteristic of geopolymer [29]. The crystalline peaks observed are associated with starting materials. There are no significant differences in phases observed with the increase in POFA replacements at 28 days, suggesting that the variability observed may not be as a result of the mineralogical content of the geopolymer.Figure 5
X-ray diffraction of 28-day ambient cured geopolymer.


## 3.1. Effect of POFA Blend on the Stress-Strain Behavior

The flexural stress-strain curves of three specimens at 28 days each from the 20 specimens of 100% metakaolin, 50% POFA, and 70% POFA are illustrated in Figure1. All the three samples show abrupt failure at varying peak stresses with the strains at failure being 0.003, 0.0028, and 0.0024, respectively, and the absence of the plastic range indicating the brittleness of the material. Apart from stress decrease with increase in POFA, blending with POFA does show the influence on brittleness given the reduction in the steepness of the stress-strain curves with increasing POFA. Brittleness is attributed to the existence of high geopolymerization products [24].Figure 1
Influence of POFA on stress-strain behavior geopolymer specimen.


## 3.2. Regression Analysis of Geopolymer Weibull Plots

The linear fitting of experimental data in Figures2 and 3 indicates adequate regression coefficient (R
2) of the plots. The model terms for the different mixes are indicated on the graphs. To further confirm the closeness of the test data with the regression data, analysis of variance (ANOVA) was performed. Only the ANOVA of mix with 100% metakaolin is presented in Table 3. The ANOVA tests confirmed that, at 0.05 levels, the regression data is not significantly different from the test data for all the mixes. Similar results were obtained in all the mixes confirming the adequacy of the Weibull regression models.Table 3
One Way ANOVA of 100% metakaolin geopolymer Weibull regression.
DF
Sum of Squares
Mean Square
F Value
Prob >F
Model
1
1.64034
E
-
6
1.64034
E
-
6
1.073222E − 6
0.9918
Error
38
58.08007
1.52842
Total
39
58.08007
Homogeneity of Variance Test
Model
1
0.00931
0.00931
0.01583
0.90054
Error
38
22.35035
0.58817Figure 2
Weibull graph of flexural strength of blended geopolymer.Figure 3
Weibull graph of compressive strength of blended geopolymer.Tables4 and 5 illustrate the comparison between Weibull and normal distribution parameters. The Weibull characteristic strengths for the mixes are more conservative when compared to those evaluated for normal distribution, for instance, at the usual 0.05 significant levels. From the study of Tumidajski et al. [8] it is not obvious that the Weibull modulus directly depended on the characteristic strength and as such it cannot be concluded here also that obvious relationship exists.Table 4
Comparison of Weibull and Normal Distribution Parameters for Flexural Strength.
Mix
Weibull
Normal
Characteristic Strength (MPa)
Modulus
Mean Strength (MPa)
Standard Deviation
100%  MK
14.35
9.76
13.64
1.69
50% POFA
11.97
11.55
11.45
1.18
70% POFA
9.47
16.59
9.08
0.65Table 5
Comparison of Weibull and Normal Distribution Parameters for Flexural Strength.
Mix
Weibull
Normal
Characteristic Strength (MPa)
Modulus
Mean Strength (MPa)
Standard Deviation
100%  MK
67.40
15.56
67.12
5.22
50% POFA
60.58
14.74
58.41
5.03
70% POFA
48.95
12.37
43.83
4.04


## 3.3. Effect of Blending on Strength Distribution

Using Weibull plots of Figure3 to study the effect of blend on the distribution of the strength, it was observed that, generally, the Weibull modulus for flexural strength increased with replacement of metakaolin by POFA, indicating that flexural strength variability reduces with increase in POFA content. It can be observed in Figure 2 that the slope of the line for the 100% metakaolin geopolymer is 9.763 which is an estimate of Weibull modulus for the set of pure metakaolin specimens. A slope of 11.3 was obtained from specimens with 50% POFA replacement while that for 70% POFA replacement is 16.69 which are in tandem with the brittle behavior of Figure 1. This tends to indicate that the ceramic-like behavior (wide strength distribution) of the geopolymer samples reduces with increase in POFA replacement considering that modulus for ceramics lies between 3 and 12 [6].The microstructure of specimens prepared from 100% metakaolin revealed heterogeneous grain comprising loose structured precipitates forming around the sheetlike packing of unreacted metakaolin with interconnected pores (Figure4(b)). This may be responsible for the broad characteristic strength of the specimen as the sheetlike arrangement with micropores gives way to more homogenous densely packed microstructure with reduced micropores as the POFA replacements in the specimens increased to 50% and 70%. The Si/Al ratio of 100% metakaolin which is less than 3 (Si/Al = 2.41) leads to the formation of geopolymer with stiff and brittle properties as its three-dimensional structure of cross-linked rigid networks [25] fails abruptly in the presence of flaws such as voids (Figure 4(b)). The higher Si/Al ratios of 50% and 70% POFA blended geopolymers (Si/Al = 4.49 and 6.72) tend to form a less rigid structure transiting from a three-dimensional to a two-dimensional network. The wriggles observed in the curves of 50% and 70% POFA (Figure 2) may be attributed to flaws from volume distributed relics of POFA in the microstructure [9]. The pure metakaolin specimen has the lowest Weibull modulus falling in the range of ceramic material (3 to 12). That for 50% POFA replacement barely falls in the range while that for 70% replacement is outside the range of ceramic. The implication of this is that the pure metakaolin system with the lowest Weibull modulus has broad flexural strength distribution and that for 70% has narrow flexural strength distribution with 50% falling in-between. As earlier mentioned, narrow distribution is a feature of a relatively homogeneous distribution of flaws. Material presenting narrow strength distribution is preferable because such a material is more predictable and has the least chance of failure at a stress lower than the characteristic value [9].FESEM of metakaolin powder and geopolymer specimens.
(a)
Metakaolin powder
(b)
100% MK geopolymer
(c)
50% POFA geopolymer
(d)
70% POFA geopolymerThe Weibull modulus for compression strength of 100% metakaolin and 50% and 70% POFA replacement is shown in Figure3. The modulus for geopolymer with 100% metakaolin and 50% and 70% POFA is 15.557, 14.070, and 12.367, respectively. This shows that variability is the highest for geopolymer with 70% POFA and the lowest for that with 100% metakaolin under compression loading.It is interesting to note that while the strength variability increased with POFA replacement in compression test, the opposite is the case for bending strength. Also, Weibull variability trends in compression also differ from that of a normal distribution of Table4. This may be due to the fact that Weibull variability results mainly from flaws in the material structure. Furthermore, fracture in bending is mainly influenced by micropores which are seen to be predominant in the pure metakaolin system (Figure 4(b)) while variability in compressive failure may be due to heterogeneity caused by unreacted POFA which are noticeable in Figures 4(c)and 4(d). The failure mode in compression may be as a result of slow propagation of many cracks that coalesced to create a crushing zone as against the rapid and unstable crack development typical of flexural failure [8]. While the presence of reaction relics may be playing a major role in the crushing failure of specimens, the micropores may be the dominant factor responsible for scatter in flexural failure.


## 3.4. Effect of Blending on Characteristic Strength

The Weibull characteristic flexural strength obtained at 63.2% probability of fracture is the highest with a value of 14.339 MPa for the geopolymer samples prepared with 100% metakaolin (Figure2). Characteristic strength values reduced with increasing POFA replacement to give values of 12.013 MPa and 9.38 MPa for 50% and 70% POFA replacement, respectively. The characteristic flexural strength gives an indication of the fracture toughness of the material as an increase in strength depicts increase in fracture toughness [26]. The higher characteristic strength for pure metakaolin based geopolymer may therefore result in high fracture toughness even though it manifested relatively broad band distribution of brittle materials.In a similar manner, characteristic compressive strength decreased with POFA replacement as indicated in Figure3. The characteristic compressive strengths are 69.4 MPa, 60.58 MPa, and 46.95 MPa for 100% metakaolin and 50% and 70% POFA, respectively.The trend of both characteristic flexural and compressive strengths due to POFA replacement may be as a result of Si/Al ratio of the primary material which plays a major role in the strength of geopolymer. The availability of silica and alumina influences the extent and rate of polymeric reaction. Hypothetically, the strength of the geopolymer should increase with increase in the Si/Al ratio because Si–O–Si bonds, which are stronger than Si–O–Al and Al–O–Al bonds, should be more with increase in Si/Al ratio. This is however usually not the case due to some other synthesis factors [27]. Increase in POFA replacement raises the Si/Al ratio from 2.41 for pure metakaolin geopolymer to 4.49 and 6.72 for 50% and 70% POFA mixes, respectively. The high volume replacement with POFA may prevent complete reaction of the materials leaving behind relics as observed in Figures 4(c) and 4(d). The reduction in strength may therefore be due to the existence of these relics that have not been used in the polymerization process. They form the volume distributed flaws that act as the “weakest link” in the microstructure, thus becoming the major determinant of the fracture strength of the material.


## 3.5. Field Emission Scanning Electron Microscopy

Field emission scanning electron microscopy (FESEM) micrographs of metakaolin starting material are shown in Figure3 and those of geopolymer specimen are shown in Figures 4(a), 4(b), 4(c), and 4(d). The gel formation in the microstructure of the metakaolin geopolymer is shown in Figure 4(b) to be predominantly formed to take after the platy sheets of metakaolin. This arrangement does not allow for complete filling of spaces between the sheets by the gel. The micropores also observed by Hawa et al. [28] vary in volume and size within the entire microstructure. The marked difference in grain direction of the sheets which are irregularly arranged could result in varying the induced microresistance to applied load by different specimen depending on the nature of formed gel laminates and hence the broad distribution of strength at failure observed in flexural loading.The micrograph of 50% POFA specimen in Figure4(c) presents less packed gel laminates that take after the metakaolin particle shapes in the microstructure. The reduced presence of the sheetlike grains suggests a better consistency in the gel formation that may be responsible for the reduced flexural strength variability. However, there exist some artifacts from incomplete reaction of metakaolin rubbing off on the homogeneity of the microstructure. The relics which appeared to be minimally distributed tend to have influence on the variability of compressive strength in a similar manner. Figure 4(d) showing the micrograph of 70% POFA mortar revealed a microstructure with a noticeable presence of POFA relics and absence of the platy grain gel.


## 3.6. X-Ray Diffraction

The XRD patterns of the geopolymer mortar are shown in Figure5. The broad band and low intensity patterns exhibited between 24° and 28° at 2-theta angle for three specimens indicate a high degree of amorphous structure of the mortar which is characteristic of geopolymer [29]. The crystalline peaks observed are associated with starting materials. There are no significant differences in phases observed with the increase in POFA replacements at 28 days, suggesting that the variability observed may not be as a result of the mineralogical content of the geopolymer.Figure 5
X-ray diffraction of 28-day ambient cured geopolymer.


## 4. Conclusion

Based on the results obtained in this study, the following conclusions can be made.(
1
) Weibull distribution can be used to characterize the flexural and compressive strength distribution of geopolymer blended with high volume metakaolin and POFA. It can also be used to prescribe the threshold value of a reliable strength of the blended geopolymer depicted by the Weibull characteristic strength.(
2
) The Weibull distribution used to characterize the flexural strength distribution of metakaolin blended geopolymer showed that the pure metakaolin geopolymer specimen has the least homogeneity with broad flexural strength distribution as depicted by the Weibull modulus meaning that blend with POFA improves the strength distribution of the POFA blended geopolymer through the filling of the porous microstructure by reaction products of metakaolin and POFA. On the other hand, the compressive strength distribution of the specimens increased with POFA is attributed to the influence of heterogeneous reaction relics of the system.(
3
) The characteristic flexural and compressive strengths of the specimens generally reduced with POFA blend with the 70% POFA blend having the least strength mainly as a result of increase in Si/Al ratio leading to existence of reaction relics.



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*Source: 658067-2014-08-31.xml*