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1. Introduction

Owing to rapid industrialisation, there has been an increase in power generation, with numerous coal-powered electricity stations being used currently at high to maximal capacities. This has resulted in increased amounts of by-products being produced from the coal combustion process in these power stations; these products include fly ash, cenospheres, and bottom ash [1]. Of these, there has been increasing focus on the utilisation of fly ash since it is the major component, which is collected in electrostatic precipitators [2]. Recent estimates indicate that the annual global production of fly ash is ~800 mT [3]. Unused fly ash generally is stored on-site at power stations in containers or in a slurry form in collection ponds [4]. The former strategy creates problems in terms of space requirements for storage while the latter can be subject to leaching of toxic elements from the fly ash [4]. Dumping of fly ash into water resources is known to occur in some countries, leading to major environmental issues [5]. These volumes illustrate the need for novel strategies for the utilisation of fly ash since only 20–50% is used commercially [3], with the major application being for the cement industry as pozzolan/aggregate [6]. However, higher utilisation in some European countries is the case as they produce very low volumes, although the utilisation levels by major producers in Asia and North America are low [3].

Fly ash consists of whitish spherical particles of size in the range 1–200 µm, with average sizes being 20–40 µm [4]. Fly ash may contain remnants of unburnt carbon from the coal, which makes it appear grey to black in colour. Moreover, it may contain varying amounts of iron oxide, which can generate colours ranging from light to dark brown [4]. The proportions of the different oxides in fly ash vary with the source of the coal and the combustion process. On the basis of composition, the major oxide components are Al2O3 and SiO2, which result from the fact that clay and sand are the principal mineral phases of coal. While SiO2 is the major component of the glassy spherical particles, undissolved α-quartz (SiO2) generally is the principal crystalline phase. Another significant crystalline species that form during coal combustion is mullite (3Al2O3·2SiO2) while lower levels of magnetite (Fe3O4) and/or hematite (Fe2O3) also are observed commonly [7]. While Class F fly ashes are low in CaO, Class C fly ashes have higher CaO contents [8], which have been observed by the authors to be >10 wt% CaO. Mullite is generally seen as a reaction product from reactions of Al2O3- and SiO2-containing materials [9].

The widespread presence of mullite in fly ash suggests the applicability of such fly ashes as sources of mullite-based products. High-temperature applications are suggested by mullite’s high melting point of 1850 °C, as shown in the Al2O3-SiO2 phase diagram of Figure 1a [10]. Other advantageous attributes of mullite are its stability in both oxidising and reducing atmospheres [11]; moderate coefficient of thermal expansion, which generally is in the range α25–1000 = ~4.5–6.0 × 10−6 °C−1 [12]; good thermal shock and spalling resistance; high shear modulus; low thermal conductivity; good resistance to acidic and neutral slags; and excellent general corrosion resistance.

However, the applicability of fly ash as a source of mullite-based refractory products is challenged by its high glass content, the softening of which is well known as the principal source of high-temperature deformation of many oxide ceramics [13]. As shown in Figure 1b, the heating of highly vitreous bodies such as fly ash, which generally contain ~60–70 wt% glass [14], would be expected to result in sigmoidal firing shrinkage kinetics. That is, initial slow glass softening at high glass viscosities would enhance particle rearrangement and firing shrinkage, followed by slumping owing to rapid deformation at low glass viscosities.

As suggested in Figure 1a, the stoichiometry of mullite ranges from an Al2O3:SiO2 molar ratio of 3:2 to 2:1 [9,12]. Single-crystal mullite is observed in the form of acicular (needle-like) or equiaxed grains, the morphologies of which vary with the Al2O3:SiO2 ratio, with lower Al2O3 contents’ (viz., 3:2 mullite) resulting in more anisotropic grains [12]. Further, the morphology is affected by the addition of oxides (e.g., Fe2O3 enhances anisotropy [12]), which may be related to the effect of the additive on the glass viscosity, while anisotropy is restrained by high glass viscosities from low-fluxing additives (e.g., Cr2O3 [15]). While mullite is of the orthorhombic crystal structure, the preferred growth direction of mullite needles is [001] [16,17,18]. Although there are several reports of high-temperature axial thermal expansions, interpolation of the most comprehensive set of data [19] for 3:2 mullite gives the following axial and bulk coefficients of thermal expansion:

  • a-axis: α20–1000 = 5.39 × 10−6 °C−1
  • b-axis: α20–1000 = 7.73 × 10−6 °C−1
  • c-axis: α20–1000 = 7.10 × 10−6 °C−1
  • Bulk: α20–1000 = 6.74 × 10−6 °C−1

Although mullite-containing materials are used commonly as commercial refractory products, the mineral mullite is not available as a bulk raw material for refractory fabrication [20]. Consequently, mullite generally is produced by heat treatment of other aluminosilicates, including kaolinite (Al2O3·2SiO2·2H2O), andalusite/sillimanite/kyanite (Al2O3·SiO2), or pyrophyllite (4SiO2·Al2O3·H2O) at temperatures ≥1200 °C, although these products consist of glass-bonded aggregates [12]. The different mullite-based refractory products are classified according to their Al2O3 contents and related pyrometric cone equivalents (PCEs) into fireclay (~25–45 wt% Al2O3; PCE = 31–35), aluminous (~45–65 wt% Al2O3; PCE = 35–38), and mullite (~65–75 wt% Al2O3; PCE = 38–39) products [20,21].

The refractoriness of mullite in principle is rated at 1850°–1865 °C (PCE = 38–39) [22] but the actual performance is somewhat lower owing to glass softening and resultant firing shrinkage. In practice, pure single-phase mullite exhibits short-term creep resistance at temperatures ≤1400 °C and commercial mullites perform similarly only to ≤1000 °C [13]. This degradation in practice highlights the importance of the achievement of direct bonding between the mullite grains in contrast to chemically (glass) bonded refractories, the thermal properties of which are dominated by the glassy matrix [23].

While the thermal resistance is a critical factor in refractory performance, chemical resistance often is an essential quality in metallurgical applications. Mullite-containing refractories are used commonly as linings for molten aluminium-alloy holding furnaces [24]. In these refractories, the molten metal wets and corrodes the refractory, which leads to the reduction of the siliceous component of mullite and the resultant formation of Al2O3 as a by-product. However, the corrosion resistance can be improved by the addition of non-wetting additives that react with mullite to form complex oxides that increase the alloy wetting resistance of the refractory surface [25,26,27,28,29].

More broadly, the corrosion resistance of mullite to some transition metals, such as Ti, V, Fe, Zn, and Zr is poor [12]. However, its corrosion resistance to Ni is good, which suggests the possibility of that mullite may be suitable for containment of Ni-based superalloys. There do not appear to be any studies of the corrosion resistance to Co-based superalloys.

Table 1 summarises the published literature on the production of mullite from fly ash. These data reveal that the foci of much of this work were the modification of the Al2O3:SiO2 ratio to shift it nearer to the stoichiometric 3:2 mullite ratio (~71.8 wt% Al2O3, 28.2 wt% SiO2) and to produce porous mullite products. The production of porous bodies generally involves the use of AlF3, which tends to produce gaseous SiF4 upon reaction with the SiO2-rich glass present in these compositions, which removes the glass and creates porosity. More critically, heating was done for a maximal time of only 4 h in all of these studies (except for one where they formed whiskers at a relatively lower temperature) and none reported the long-term firing shrinkages. The combination of these factors represents the principal difference between these works and the present work, which reports the development of unique, dense, mullite microstructures revealed by firing shrinkage measurements and that are generated using high-SiO2 compositions and long-term heating. This novel composition and microstructure, which consists of percolated mullite, exhibits unparalleled high-temperature stability owing to the achievement of a continuous, direct-bonded, single-crystal network of mullite needles [30].

2. Percolated Mullite

Highly dense 3:2 mullite (<2% apparent porosity) with microstructures completely percolated throughout the entire sample volumes were fabricated using either fly ash alone or fly ash mixed with an oxide addition at a low concentration [30,56]. These intergrown microstructures developed through mullite nucleation (small equiaxed precipitated grains of primary mullite) and growth (elongated grains of secondary mullite from primary mullite and pre-existing mullite needles). Although percolation can be achieved using fly ash alone, the kinetics of percolation can be enhanced through the addition of different additive types and amounts. A key but counter-intuitive feature of the generation of percolated mullite is the presence of excess SiO2-rich glass. This glass acts as both a medium for the diffusion of ions for mullite growth at high temperatures but also provides a deformable medium that is compliant with the axial and diametral growth of the mullite needles. Once these needles have grown to sufficient lengths, they form direct-bonded intergrowths that completely exclude any glass between the grains [57], thereby forming a non-shrinking single-crystal network that exhibits the intrinsic properties of pure mullite on a full volumetric basis [56,57]. Critically, this percolated microstructure isolates any residual glass within the triple points, effectively forming a 0–3 composite [58,59] whose thermomechanical properties, including high-temperature strength and creep [56], are unaffected by the glass. The thermal expansion would be expected to be increased by the glass but this effect would be mitigated by resistance from the rigid, continuous, mullite skeleton.

The percolated mullite was developed and patented over the period 2012–2016 from a range of Class F fly ashes from Australia and China; typical compositions for these are shown in Table 2. These fly ashes contain glass as the major component, with minor crystalline phases of mullite and α-quartz plus trace amounts of magnetite and α-hematite.

The pure fly ash compositions were uniaxially pressed into cylindrical pellets (15 mm diameter × 5 mm height), heated to 1500 °C (heating rate 120 °C/h), and soaked for 1–96 h. Figure 2 shows the changes in mullite needle dimensions (lengths and width) with increasing heat treatment time. All of the microstructures were etched with HF and then characterised using scanning electron microscopy (SEM). The samples were not carbon coated since this could have impacted on the imaging resolution between the individual needles. However, the result of this was some charging of the samples, as indicated by the lighter coloured regions in the images. It can be seen that the well-formed but discrete mullite needles formed at only 1 h but these developed into a continuous interconnected network by 4 h. At the longer time points, the main difference was needle coarsening, increasing aspect ratio, and some exaggerated grain growth.

Importantly, the diametral firing shrinkages were determined at each sintering time. Figure 3 shows the diametral firing shrinkage trends of the pure fly ashes (1, 2, and 3) and fly ash 3 with α-Al2O3 added in order to shift the overall composition toward that of mullite (~46 wt% α-Al2O3). These data clarify that that percolation, indicated by the cessation of further volumetric firing shrinkage, can be achieved at a soak time of only 2 h at 1500 °C.

It is somewhat surprising that, despite the differences between the fly ashes in terms of amount and type of glass and the amount of mullite, percolation could be achieved consistently at soak times of ~2–4 h. The major differences were manifested in the extents of firing shrinkage for pure fly ashes and in the kinetics of firing shrinkage for the fly ashes with α-Al2O3 added. The principal driving force for these differences is shown in Table 2, which reveals significantly different (1) Al2O3/SiO2 wt% ratios, (2) amounts of fluxing impurities (e.g., Na2O, K2O, CaO, and Fe2O3), (3) resultant glass viscosity, and (4) amounts of unburnt carbon (shown by the loss on ignition, LOI). The first of these variables would affect both the glass viscosity but also the ultimate mullite content. The second of these would affect the glass viscosity but also the tendency to favour the formation of equiaxed or needle-like mullite [12]. The last of these would affect the firing shrinkage upon oxidative gas emission.

When comparing the firing shrinkage behaviour of samples fabricated using only fly ashes with those fabricated using mixtures of fly ash and calcined alumina, it is clear that the addition of α-Al2O3 has an insignificant effect at low additions (<20 wt%) and a retarding effect at high additions (>20 wt%) on the achievement of percolation. This clearly reflects the role of Al2O3 in increasing the glass viscosity, as suggested in Figure 1a. When α-Al2O3 is added, the diametral firing shrinkage shows a fluctuation (viz., expansion) at 4 h, which was observed in fly ash 1. This expansion is interpreted in terms of the sequence prior to percolation described in Table 3.

It also is possible that the expansion derived from gas exudation upon the achievement of sufficient reduction in glass viscosity and resultant microstructural disruption but these are not consistent with the LOI levels shown in Table 2.

The preceding considerations clarify the reasons for the failure of previous studies to report volumetric percolation. That is, in addition to the use of soak times generally insufficient to achieve percolation and the non-measurement of firing shrinkages, the glasses at issue were of high viscosities such that the necessary diffusion and compliance for mullite percolation were not established because (1) the studies of pure fly ash involved high-Al2O3 types and (2) the studies of fly ash with Al2O3 added were designed to equate to the mullite composition.

Image analysis of the SEM images was conducted to quantify the microstructural changes occurring during heat treatment as a function of soak time. For each SEM image, ~500–1000 grains (depending on time) of mullite were measured in order to provide statistically significant quantification of the needle lengths in terms of the values D10, D50, average, and D90, as shown in Figure 4a. The data in Figure 4b show that the needle lengths and areal coverage of the microstructure increased significantly with increasing sintering time up to 24 h, with the most of the significant alterations occurring within ~4 h. Soaking for longer times reduced the number of mullite needles owing to grain growth, terminating in areal coverage of ~96% and a maximal needle length (for fly ash 2) of ~15 μm.

The kinetics to achieve percolation also can be manipulated through the addition of oxides that modify the glass viscosity. Figure 5 summarises the impacts of three additives: MgO (1 wt%), CaO (0.5 wt%), and Fe2O3 (2 wt%). Comparison of Figure 3b and Figure 5 shows the general enhancement of the rate of percolation from the oxide additions. These data also reveal that α-Fe2O3 was more effective than MgO or CaO, which reflects a combination of the solidus temperatures of the respective systems and the amounts of the additives:

FeO-Al2O3-SiO21083 °C(1.8 wt% addition)[60]
Fe2O3-Al2O3-SiO21382 °C(2.0 wt% addition)[61]
MgO-Al2O3-SiO21355 °C(1.0 wt% addition)[60]
CaO-Al2O3-SiO21170 °C(0.5 wt% addition)[60]

The data for the equivalent FeO from α-Fe2O3 are included because reduction of the latter to the former is a common occurrence during the heating in air of thick ceramics owing to oxygen starvation of the interior of the compact, as is evidenced frequently from the black coring of Fe-rich bricks [62]. The additions in the present work represent maximal addition levels as higher amounts resulted in excessive vitrification, loss of sample shape, and prevention of mullite percolation.

Figure 3, Figure 4 and Figure 5 show that percolation can be achieved in ~2–4 h for fly ashes both without and with oxide addition, resulting in a 0–3 [58,59] glass-mullite composite consisting of a dense, continuous, single-crystal, mullite skeleton with glass isolated in the triple points. These data also show that there is only insignificant microstructural alteration after heating at 1500 °C for ~24 h, so the grains undergo little additional grain growth. These data also show that the conventional logic of addition of Al2O3 to achieve a net mullite composition prevents the detection of percolation owing to high glass viscosity, insufficient glass content, and low ionic diffusion, all of which result in the formation of a porous polycrystalline conglomerate. Further, Figure 5 shows that oxide additions, such as α-Fe2O3, offer the potential to achieve percolation with higher Al2O3 contents (40 wt%) approaching that of mullite (48 wt% Al2O3 for fly ash 3) to achieve a net mullite composition), albeit with slower kinetics to achieve percolation but at a lower residual glass content.

The selection of the type and amount of additive to enhance the kinetics of percolation will be dependent on the nature of the fly ash (especially its Al2O3:SiO2 ratio), the fluxing effectiveness of the oxide addition, the soak temperature, and the soak time. Examination of these variables has the potential to (1) increase the kinetics of percolation by reducing the temperature and/or time required for percolation or (2) reduce the kinetics of percolation while decreasing the amount of residual glass in the triple points.

As discussed previously, the major advantage of percolated mullite over conventional mullite products is the microstructure consisting of a direct-bonded, single-crystal, continuous, needle network that prevents high-temperature deformation and isolates the residual glass in the triple points. These characteristics allow percolated mullite to exhibit unprecedented thermal stability to at least at 1600 °C, as shown by the diametral shrinkage data in Figure 3, Figure 4 and Figure 5 and the thermal expansion data in Figure 6. In principle, if slip systems are not activated to cause high-temperature deformation, the performance may extend as high as the melting point of mullite (1850 °C).

These data suggest that the thermal expansion is dominated by the [010] and [001] axial directions of the mullite needles. The expansion at 1000 °C, which is higher than the reported bulk expansion of α20–1000 = 6.74 × 10−6 °C−1, may derive from the additive effect of the residual glass in the triple points but it also may be due to differences in the mullite samples and/or the measurement techniques.

These microstructures also can be tailored to exhibit specific properties. At high porosities, the microstructures can be engineered to moderate the low thermal conductivities and low compressive strengths. At low porosities, highly dense microstructures containing only closed spherical pores can be engineered [56] for low thermal conductivities but high compressive strengths [63]. Furthermore, manipulation of the microstructure can be done to create highly dense bodies with small closed spherical pores which help to also lower the thermal conductivity.

Consequently, percolated mullite has been used to fabricate dense and porous sintered refractory shapes, aggregates, and porous refractory shapes from sintered aggregates fabricated from fly ash and oxide additions [56]. These refractory shapes exhibited the physical properties described in Table 4.

3. Summary The present work considers previous work on the fabrication of mullite from fly ash and introduces a novel form of volumetrically percolated mullite with microstructures consisting of direct-bonded, single-crystal, continuous, needle networks, with the residual glass isolated in the triple points. These unique microstructures exhibit unprecedented long-term high-temperature dimensional stabilities upon long-term heating at 1500–1600 °C and possibly higher temperatures. Percolated mullite can be fabricated from both pure fly ash and fly ash with oxide addition, enabling the engineering of the kinetics of percolation to moderate the thermal conductivities and compressive strengths. The application of these novel materials as acidic and neutral refractories has both economic and environmental advantages as they have the potential to utilise high volumes of fly ash, which is a low cost industrial-by product.

Figure 1.(a) Al2O3-SiO2 phase diagram, assuming congruently melting mullite (adapted from [10]) and (b) typical firing shrinkage curves for refractory products on sintering at high temperatures.

Figure 2. Microstructural variations in pure fly ash 2 samples sintered at 1500 °C for different times (a) 1 h, (b) 4 h, (c) 24 h, and (d) 96 h.

Figure 3.(a) Diametral firing shrinkages of pure fly ashes (1, 2, and 3) after sintering at 1500 °C for ≤96 h, (b) Diametral firing shrinkages of fly ash 3 with alumina additions after sintering at 1500 °C for ≤24 h (Adapted from [30]).

Figure 4. Fly ash 2: (a) changes to needle dimensions and their proportion with increasing sintering time at 1500 °C, (b) Changes to needle numbers and areal coverage with increasing sintering time at 1500 °C (Adapted from [30]).

Figure 5. Diametral firing shrinkages of fly ash 3 + alumina compositions at 1500 °C for extended times with the addition of (a) 1 wt% MgO, (b) 0.5 wt% CaO, and (c) 2 wt% Fe2O3 (Adapted from [30]).

Figure 6. Optical dilatometry data for thermal expansion of percolated mullite from fly ash 2.

No. Raw Materials Sintering Temperatures (°C)/Time Microstructural Features and Mullite Morphologies Observations Ref.
1Fly Ash/Bauxite1000°–1600 °C/4 h
  • Porous microstructures at lower temperatures
  • Denser microstructures at 1600 °C
  • At temperatures <1300 °C, cristobalite reacted with alumina to form secondary mullite.
  • Above 1400 °C, mullite was the only crystalline phase in the sintered samples.
  • Samples sintered at 1600 °C for 4 h had closed porosity of 5.44% and open porosity of 0.62%.
[31]
2Fly Ash/Ammonium Alum/Sodium Dihydrogen Phosphate1300 °C/10 h
  • Whiskers (aspect ratio of >30; 0.6–1.8 μm diameters)
  • Mullite whiskers were formed by reaction at 1300 °C for 10 h.

  • Whiskers had a composition of 47.11 mol% SiO2 and 52.89 mol% Al2O3.

[32]
3Fly Ash/ Bauxite/V2O5/AlF31200°–1500 °C/2.5 h
  • Porous microstructures (without additives)
  • Denser interlocked mullite microstructures (with additives)
  • Porous microstructures consisted of rod-like mullite crystals with no additives.

  • Addition of 4 wt% AlF3 and 3 wt% V2O5 was optimal in creating interlocked mullite microstructure with 50% open porosity; secondary mullite formation was enhanced by V2O5 addition.

  • Interlocked mullite whiskers exhibited aspect ratios ≤18.
[33]
4Fly Ash/Bauxite/TiO21300°–1500 °C/2 h

  • Porous microstructures with gradual densification with increasing TiO2 amounts

  • Samples sintered at 1450 °C for 2 h exhibited the lowest firing shrinkage and bulk density and the greatest open porosities at TiO2 contents of 0–6 wt%.

[34]
5Fly Ash/ Al(OH)3/Al2O3/AlF31400°–1600 °C/4 h
  • Reinforced needle-like whiskers

  • Long whiskers with Al(OH)3 addition

  • Short whiskers with Al2O3 additions

  • Granular particles with AlF3 additions
  • Interlocked needle-like mullite whiskers were formed.
  • This microstructure enhanced the bend strength of porous mullite, with a value of 100 MPa at an apparent porosity of ~55% after sintering at 1550 °C.
[35]
6Fly Ash/ Bauxite/V2O51100°–1500 °C/4 h
  • Puncheon-shaped (aspect ratio of 6) to equiaxed mullite crystals

  • Increasing V2O5 content at 1500 °C increased the apparent porosity and water absorption.

  • Mullite morphology changed from small puncheons to large cuboids with increasing temperature.
[36]
7Fly Ash Hollow Spheres (FAHSs)1250°–1400 °C/3 h
  • Individual hollow spheres bonded to form foam
  • Elongation of mullite grains on FAHS shells with increasing temperature
  • Fracture mechanism of FAHS ceramic foams changed from intergranular to transgranular when temperature increased from 1250° to 1400 °C.
  • Higher compressive strengths of ~6.7 MPa observed after sintering at 1400 °C were attributed to the formation of strong necking between FAHS during sintering.
[37]
8Fly Ash/Bauxite/MgO1300°–1500 °C/ 2 h
  • Needles in glassy phase
  • Needle interlocking at 1500 °C
  • MgO addition promoted densification and increased the strengths after sintering at >1400 °C.
  • MgO additions resulted in the formation of low-expansion α-cordierite at 1300 °C while corundum and spinel were formed at 1400 °C.
[38]
9Desilicified Fly Ash1300°–1600 °C/ 4 h
  • Lath-like mullite crystals that interlocked to form a framework structure filled with glassy phase at 1600 °C
  • Desilicified fly ash exhibited superior physical and mechanical properties compared to samples from fly ash.
  • Lath-like and needle-like mullite crystals formed in high-iron and low-iron samples, respectively.
  • Lath-like structures increased the flexural strengths compared to those with needle-like structures.
[39]
10High-Aluminium Fly Ash1200°–1600 °C/2 h
  • Network structure of anisotropic grains (10 μm lengths) with minimal glass phase

  • Alkali and acid treatment were done in order to increase the Al2O3 content to ~65 wt% while removing impurities.

  • Samples sintered at 1600 °C exhibited apparent porosity, bulk density, and compressive strength of 1.2%, 2780 kg·m−3, and 169 MPa, respectively.

[40]
11Fly Ash/ Bauxite/Potash Feldspar/SiC/V2O51450°–1550 °C/2 h
  • Prismatic mullite crystals forming interlocking microstructure
  • With 0 to 15 wt% SiC addition, prismatic mullite crystals increased in number, which increased the thermal conductivity and strength.
  • With 12 wt% potash feldspar addition, the compressive strength increased and the thermal conductivity reduced relative to the preceding; samples survived seven thermal shock cycles.
[41]
12Fly Ash/SiC/MoO3850 °C/2 h 1000 °C/1 h
  • Increased rod-shaped mullite crystals (from 0.8 μm to 10 μm) at higher temperature

  • 5 wt% MoO3 addition resulted in achievement of the optimal strength of the mullite-bonded SiC.

[42]
13Fly Ash/Boehmite Sol900°–1300 °C/2 h
  • Prismatic crystallites (<0.3 μm) from 4 wt% boehmite addition
  • Prismatic crystallites (0.3–1.0 μm) from 12% boehmite addition
  • Optimal mullite content (63.8%) was achieved with 12 wt% boehmite with sintering at 1200 °C.
[43]
14Fly Ash/Al(OH)3/MoO31100°–1500 °C/2 h

  • Increased liquid phase formation and larger aspect ratios of interlocked mullite whiskers from increasing MoO3

  • With 0 to 20 wt% MoO3 addition, open porosity significantly increased from 42% to 58% with sintering at 1300 °C.

  • 20 wt% MoO3 addition increased the flexural strength at higher sintering temperatures.

[44]
15High-Alumina Fly Ash/HF/NaOH1100°–1400 °C/2 h
  • Cubic puncheon-shaped mullite crystals
  • Alkali-activation treatment adjusted the chemical composition to that of stoichiometric mullite.
  • 100% fly-ash-based ceramic tiles sintered at 1300 °C exhibited optimal postsintered densification.
[45]
16Fly Ash/Alumina/AlF31000°–1400 °C/2 h

  • Increased distribution density and aspect ratio of rod-like mullite crystals with increasing AlF3 content

  • Transition from rod- to whisker-shaped mullite with increasing temperature

  • Fly ash with 6 wt% AlF3 sintered at 1200 °C exhibited lower apparent porosity and higher flexural strength than that of samples prepared from HCl-pickled fly ash.

[46]
17Fly Ash/Na2SO4/ Aluminium Sulfate/HF1000 °C/3 h
  • Whiskers (aspect ratio >25, 0.06–0.3 μm widths)
  • Mullite whiskers were prepared by varying the additive ratios
[47]
18Fly Ash/Bauxite/ Kaolin/Potash Feldspar/ Talc/BaCO3/Pyrolusite1390 °C/2 h
  • Thin layer of interwoven anisotropic mullite crystals of well controlled crystal size
  • Network of mullite-whisker-reinforced ceramics were prepared by sintering.

  • Maximal strength and minimal bulk density resulted from composition containing 2 wt% potash feldspar, 2 wt% talc, 1 wt% BaCO3, and 6 wt% pyrolusite.

[48]
19High-Aluminium Fly Ash/NaOH1400 °C/100 min
  • Microstructures containing small numbers of 15–25 μm mullite/corundum particles and large numbers of 5–15 μm mullite/corundum particles
  • Needle-like recrystallised mullite between mullite/corundum particles
  • Sintering at 1400 °C resulted in the maximal mechanical properties and minimal apparent porosity.
[49]
20Fly Ash Cenospheres (FACs)/Kaolin900°–1300 °C/3 h
  • Homogenous microstructure with FACs in continuous mullite matrix

  • FAC/mullite composites exhibited low bulk densities (650–1380 kg·m−3), high apparent porosities (23.36–70.32%), low thermal conductivities (0.14–0.45 W·m−1K−1), and relatively high compressive strengths (1.56–32.99 MPa).

  • 50 wt% FAC + 50 wt% kaolin sintered at 1200 °C exhibited a firing shrinkage of 9.45%.
[50]
21High-Aluminium Fly Ash/HCl1300°–1500 °C/2–4 h
  • Sintered mullite needle length from as-received fly ash double that from beneficiated fly ash
  • Increasing mullite needle length with increasing sintering temperature
  • Highest compressive strengths achieved at optimal sintering temperatures of 1400 °C for the as-received fly ash and 1500 °C for the beneficiated fly ash.
[51]
22Fly Ash + Alumina + Calcite1400°–1800 °C/ Time not specified
  • 0.1–2.0 μm long rod-like mullite
  • Sintering at 1700 °C resulted in mullite formation but at 1800 °C resulted in the formation of equal amounts of mullite and corundum plus a minor amount of anorthite.
[52]
23Fly Ash/Aluminium Dross/ HCl1200°, 1500 °C/4 h
  • Acicular mullite crystals embedded in aluminosilicate glass matrix
  • Following beneficiation in 2 M HCl for 1 h, the mullite-based product was well crystallised and exhibited low thermal expansion and smooth expansion curve.
[53]
24Fly Ash/Bauxite1300°–1500 °C/Time not specified
  • Lath-like mullite crystals, glassy phase, and uniformly distributed pores

  • Sample fired at 1450 °C resulted in a bulk density of 2100 kg·m−3 and apparent porosity of ~32%.

[54]
25Fly Ash/Al2O3/Starch Filler1600 °C/4 h
  • Microstructure of interwoven mullite and glassy phase

  • Major mullite and minor corundum increased with increasing Al2O3 content.

  • Pure fly ash resulted in interwoven mullite needles and high volume of glass.
  • Al/Si molar ratio of 2.40 resulted in highest linear firing shrinkages (~29%) and compressive strengths (~2.3 MPa) with ~77% apparent porosity from starch filler.
[55]

Sample SiO2 Al2O3 Fe2O3 Na2O K2O CaO MgO TiO2 LOI Other
Fly Ash 172.222.61.10.10.50.00.21.32.10.0
Fly Ash 233.831.22.50.10.41.60.41.325.03.7
Fly Ash 368.123.61.30.22.20.70.30.92.40.3
General Range33–7518–360.8–6.00.0–0.30.4–2.60.1–4.00.2–1.00.4–1.80.5–250.5–4.0
Mullite28.271.80.00.00.00.00.00.00.00.0

Time Shrinkage Glass Viscosity Dominant Effect
<2 hSignificant contractionHighVolumetric shrinkage from softening of solid-like glass with little effect of dispersed mullite needles in deformable matrix
2–4 hMinor expansionHighVolumetric expansion from thermal expansion of solid-like glass and semi-percolated mullite needle skeleton
>4 hContinued contractionDecreasingGradual volumetric shrinkage from resultant progressively decreasing glass viscosity, and increasingly liquid-like behaviour

Refractory Bulk Density (kg·m−3) Apparent Porosity (%)
Dense and Porous Shapes~1600–2000~5–30
Sintered Aggregates~900–1100~40–50

Author Contributions

Conceptualization, P.K., S.A.K. and C.C.S.; methodology, P.K. and C.C.S.; validation, P.K.; investigation, P.K., N.H., V.Z., L.S.; resources, P.K., S.A.K., E.J.S. and C.C.S.; writing-original draft preparation, P.K., N.H., and V.Z.; writing-review and editing, P.K. and C.C.S.; supervision, P.K., S.A.K., E.J.S. and C.C.S.; project administration, P.K., S.A.K., E.J.S. and C.C.S.; funding acquisition, P.K., S.A.K., E.J.S., and C.C.S. All authors have read and agreed to the published version of the manuscript.

Funding

This research was funded by Vecor Pty. Ltd. (now Vecor Technologies Pty. Ltd.) through direct research funding and through the Australian Research Council Linkage Program (ARC-LP, grant LP150101081).

Institutional Review Board Statement

Not Applicable.

Informed Consent Statement

Not Applicable.

Data Availability Statement

Not Applicable.

Acknowledgments

The authors acknowledge the long-term financial support from Vecor Pty. Ltd. (now Vecor Technologies Pty. Ltd.), funding through the Australian Research Council Linkage Program (ARC-LP, grant LP150101081), and the subsidised characterisation facilities at the Mark Wainwright Analytical Centre, UNSW Sydney, Australia.

Conflicts of Interest

The authors declare no conflict of interest.

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Pramod Koshy

1,*,

Naomi Ho

1,

Vicki Zhong

1,

Luisa Schreck

1,

Sandor Alex Koszo

2,

Erik J. Severin

2 and

Charles Christopher Sorrell

1

1School of Materials Science and Engineering, UNSW Sydney, Sydney, NSW 2052, Australia

2Vecor Technologies Pty. Ltd., Sydney, NSW 2039, Australia

*Author to whom correspondence should be addressed.

Word count: 6700

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© 2021. This work is licensed under http://creativecommons.org/licenses/by/3.0/ (the “License”). Notwithstanding the ProQuest Terms and Conditions, you may use this content in accordance with the terms of the License.

Abstract

Fly ash is an aluminosilicate and the major by-product from coal combustion in power stations; its increasing volumes are major economic and environmental concerns, particularly since it is one of the largest mineral resources based on current estimates. Mullite (3Al2O3·2SiO2) is the only stable phase in the Al2O3-SiO2 system and is used in numerous applications owing to its high-temperature chemical and mechanical stabilities. Hence, fly ash offers a potential economical resource for mullite fabrication, which is confirmed by a review of the current literature. This review details the methodologies to utilise fly ash with different additives to fabricate what are described as porous interconnected mullite skeletons or dense mullite bodies of approximately stoichiometric compositions. However, studies of pure fly ash examined only high-Al2O3 forms and none of these works reported long-term, high-temperature, firing shrinkage data for these mullite bodies. In the present work, high-SiO2 fly ashes were used to fabricate percolated mullite, which is demonstrated by the absence of firing shrinkage upon long-term high-temperature soaking. The major glass component of the fly ash provides viscosities suitably high for shape retention but low enough for ionic diffusion and the minor mullite component provides the nucleating agent to grow mullite needles into a direct-bonded, single-crystal, continuous, needle network that prevents high-temperature deformation and isolates the residual glass in the triple points. These attributes confer outstanding long-term dimensional stability at temperatures exceeding 1500 °C, which is unprecedented for mullite-based compositions.

Details

Title
Fly Ash Utilisation in Mullite Fabrication: Development of Novel Percolated Mullite
First page
84
Publication year
2021
Publication date
2021
Publisher
MDPI AG
e-ISSN
2075163X
Source type
Scholarly Journal
Language of publication
English
DOI
https://doi.org/10.3390/min11010084
ProQuest document ID
2479580739
Copyright
© 2021. This work is licensed under http://creativecommons.org/licenses/by/3.0/ (the “License”). Notwithstanding the ProQuest Terms and Conditions, you may use this content in accordance with the terms of the License.