Utilisation of Recycled Silt from Water Treatment and Palm Oil Fuel Ash as Geopolymer Artificial Lightweight Aggregate

The global consumption of aggregate in the construction field is increasing annually, especially in concrete production. With the development of the economy and increase of the population, the demand for concrete and, therefore, a huge amount of aggregate has increased significantly. This issue is pressing and needs to be addressed. Lightweight aggregate (LWA) is one possible solution. This study investigated the potential use of artificial LWA manufactured from alkaline-activated palm oil fuel ash (POFA) with silt due to its properties and performances. Six mixes containing up to 60% silt by total weight combined with optimised activated POFA were analysed. The artificial LWA was synthesised through a pelletising and sintering process at 1150 °C. The increase in the activated POFA proportion in the mixture induced changes in the properties of artificial LWA, including the physical and mechanical properties, durability, and microstructure. The analytical results showed that all of the artificial aggregates were categorised as LWA, based on BS EN 13055. The artificial LWA with 40% activated POFA and 60% silt had the highest crushing strength and acceptable properties for construction applications. This study summarised the performances of the final products and highlighted the different uses of imported silt and POFA as building materials for minimising environmental impacts.


Introduction
The annual consumption of concrete by the construction industry worldwide has reached 1.6 billion tonnes of ordinary Portland cement (OPC), 10 billion tonnes of sand and rock, and 1 billion tonnes of water, thus making the concrete industry the largest consumer of natural resources on the planet [1]. It was reported that the concrete industry consumes about nine billion natural aggregates annually [2]. The high demand for concrete for building construction contributes to the embodied energy consumption and carbon dioxide (CO 2 ) emissions released during the production of cement. CO 2 is the most important greenhouse gas (GHG), and it is increasing in the atmosphere. It is responsible for around 70% of the greenhouse effect, which can lead to a thicker thermal blanket, thus affecting the Earth's atmosphere [3]. The exhaustion of natural resources is also an environmentally damaging factor. Hainin et al. [4] highlighted that the continuous use of natural aggregates will cause their depletion in the future. A continuous decline in granite aggregate production would affect the cost of concrete production [5]. This phenomenon has prompted many researchers to switch direction towards the utilisation of waste materials, such as fly ash, wood waste ash, slag, silica fume, and palm oil ash in the production of concrete. The use of waste materials in concrete can reduce the cost and the negative environment effects related to concrete production.
Recycling and reusing natural wastes as sustainable construction materials not only appears to be viable solution to the pollution problem, but also could be an economical option for designing green buildings. One of the approaches for reducing greenhouse pellets. The sintering method is based on atomic diffusion, which is commonly applied for the mass production of lightweight products. Combination treatment approaches can also be applied, depending on the materials used. For the sintering method, the formation of a viscous mineral matrix is accepted, but the total melting conditions should not be reached [17].
The use of an alkaline activator as a stimulator is one method for improving LWA production. An alkaline activator is widely obtained from the geopolymer as it activates the geopolymerisation reaction. It reacts with the aluminium and silicate oxides existing in any raw material to form geopolymer cement [18,19]. The suitability of the alkaline-activated geopolymer is affected by the type of alkaline activator, concentration, ratio with raw geopolymer, curing method, and regime [20,21].
This study examined the feasibility of manufacturing artificial LWA from the geopolymer POFA with silt and the performances of these combinations as artificial LWA. The optimal result of alkaline-activated POFA and sintering temperature for the production of artificial LWA was determined through a preliminary experiment. The physical and chemical structures of the primary materials were investigated. Several laboratory testing methods were also applied to assess the performance of the artificial pellets in terms of their physical and mechanical properties, durability, and microstructure.

Raw Materials Used
The POFA was a by-product obtained from the residual burning of palm oil kernel shell and fibre at a high temperature above 1000 • C, which were collected from a palm oil mill. The collected POFA was oven-dried to remove the extra moisture content and then sieved through a 300 µm sieve to remove large unwanted coarse particles. The WTS was obtained from the residue of a water treatment plant. The sludge was dried under sunlight, the large-size residues were crushed into a small size, and the resulting residues were ground into silt. The POFA and small-sized sludge were ground into fine powders of 45 and 150 µm, respectively.
The alkaline activator for POFA geopolymer was a combination of 12 M NaOH and Na 2 SiO 3 . The alkaline was used to activate the POFA for forming activated POFA geopolymer. The NaOH molarity for this study was based on the recommendations of prior related studies [22,23], which were also proved to be applicable for POFA geopolymer [24,25]. The concentration of alkaline is directly proportional to the compressive strength. However, this parameter will decrease the strength properties as the molarity exceeds the limit of Na ions to react with elements within the raw material used. The effect of the alkaline concentration on geopolymer is less significant compared to that of the other factors, such as the alkaline ratio and alkaline-to-raw ratio [25,26]. NaOH was in the solute form of Formosoda-P NaOH (reagent grade, with a 99% purity), whereas Na 2 SiO 3 was in liquid form. The specifications of Na 2 SiO 3 and NaOH are displayed in Tables 1 and 2. Both alkaline types were industrial grade and exhibited a stable performance.   3 30.10 ----9.40 -----Note: bdl = below detection limit; nd = not detected; LOI = loss of ignition.

Characteristics of Materials
The analysis of the physical properties of the raw materials, such as particle size analysis, specific gravity, and soil classification for silt, is presented in Table 1. The grind POFA contained 90% fine particles of 35 µm and medium particles (D 50 ) of 5.01 µm. The silt resulted in 50% particles with a size of 57.2 µm. This result showed that silt had a fine grain size in nature after grinding. The plastic limit, plasticity index, and liquid limit of silt were 44.49%, 24.71%, and 69.20%, respectively. The silt was considered inorganic silt, with a high compressibility, according to the Burmister classification (1949). The alkaline activator used was NaOH and Na 2 SiO 3 , and the specifications are shown in Table 1. NaOH was in pellet form, with a 99% purity and molecular weight of 40 g/mol, and it was fully water soluble.
The chemical and mineralogical compositions of the raw materials were investigated through XRF, X-ray diffraction (XRD), and scanning electron microscopy (SEM). As shown in Table 2, the main chemical composition of POFA and silt was silica oxide (SiO 2 ), and their contents were 54.98% and 43.26%. This finding was further confirmed by the result shown in Figure 1 through XRD analysis. Both materials had a high reactive silica content, which contributed to their strength ratio. Furthermore, the content of SiO 2 enhanced the formation of the 3D silica structure for the artificial LWA when sintering. POFA was categorised as a Class-C pozzolan material, according to ASTM C618-05, because it contained 10.77% of CaO and had a sum of 62.21% oxide compounds in silica, aluminium, and iron oxides (SiO 2 + Al 2 O 3 + Fe 2 O 3 ). It was also classified as a siliceous material. Thus, POFA enhanced the calcium-silicate-hydrate (C-S-H) gel formation by reacting silica within itself and silts to achieve a high strength. The reason was that the formation of the C-S-H gel helped to boost the hydration process. The high contents of SiO 2 and Al 2 O 3 present in silt indicated that it was acidic oxide. It was also suitable for use as a binding and filling agent to make a water-permeable material with comparable engineering properties [27]. The magnesium oxide (MgO) and CaO contents for silt were low due to the absence of the carbonate mineral. The silica/alumina ratio (SiO 2 /Al 2 O 3 ) for silt was 1.52. The available fluxing elements, such as Fe 2 O, MgO, CaO, sodium oxide (Na 2 O), and potassium oxide (K 2 O), confirmed the development of high-temperature glassy phases with a sufficient viscosity. The chemical composition of the flux for raw materials satisfied the requirement stated by Riley (1950) within the range of 4.5-31%.
The loss of ignition (LOI) of the POFA and silt were 5.6% and 3.3%, respectively. LOI could predict the amount of gas that needs to be released to perform the expanded aggregate. The LOI of POFA was mainly attributed to the oxidation of organic material. The LOI of POFA fulfilled the requirement of ASTM C618. The low LOI of POFA revealed some improvement, given that some little unburnt residues existed, which were eliminated when sintering was applied. The LOI of silt was due to the dewatering of the absorbed water or the dehydroxylation of the silt mineral at a certain temperature, such as kaolinite [28]. was expected to have a greater strength due to the high silica content. The main minerals revealed in the matrix of POFA included quartz (SiO2), kyanite (Al2O(SiO4)), and gahlenite (Ca2Al(AlSiO2)). The major synthesised crystalline phases within silt included quartz (SiO2), kaolinite (Al2Si2O5(OH)4), and rutile (TiO2). The presence of kaolinite contributed to the plasticity index of the silt. The microstructures of silt and POFA particles are shown in Figure 2. The particles in POFA were small and crushed in size and shape, compared with those in the unground POFA. The particles in the ground POFA were less porous. As the size was reduced, the ground POFA particle became irregular and gained a crushed shape in its microstructure [29]. Figure 2a shows the SEM of POFA particles with an irregular arrangement, small size, and less porous appearance. This sample revealed an uneven filler particle with few and concentrated fine particles. It showed a nonuniform distribution with fracture and pebble-shaped particles. The SEM of silt presented numerous roughly angular spherical particles (Figure 2b). The cenosphere showed an acicular structure and gave a needle plate-like structure, with some angular particles. This morphology of particle allowed silt to act as a lubricant in the interstitial space [30]. Both were varied in structure and thus had a high probability of mixing together homogeneously. XRD was used to determine the crystalline phase of the raw materials, as shown in Figure 1a,b. Significant quartz (SiO 2 ) was observed for POFA and silt. This finding could be verified by the chemical composition result, as shown in Table 2. The treated POFA was expected to have a greater strength due to the high silica content. The main minerals revealed in the matrix of POFA included quartz (SiO 2 ), kyanite (Al 2 O(SiO 4 )), and gahlenite (Ca 2 Al(AlSiO 2 )). The major synthesised crystalline phases within silt included quartz (SiO 2 ), kaolinite (Al 2 Si 2 O 5 (OH) 4 ), and rutile (TiO 2 ). The presence of kaolinite contributed to the plasticity index of the silt.
The microstructures of silt and POFA particles are shown in Figure 2. The particles in POFA were small and crushed in size and shape, compared with those in the unground POFA. The particles in the ground POFA were less porous. As the size was reduced, the ground POFA particle became irregular and gained a crushed shape in its microstructure [29]. Figure 2a shows the SEM of POFA particles with an irregular arrangement, small size, and less porous appearance. This sample revealed an uneven filler particle with few and concentrated fine particles. It showed a nonuniform distribution with fracture and pebble-shaped particles. The SEM of silt presented numerous roughly angular spherical particles (Figure 2b). The cenosphere showed an acicular structure and gave a needle plate-like structure, with some angular particles. This morphology of particle allowed silt to act as a lubricant in the interstitial space [30]. Both were varied in structure and thus had a high probability of mixing together homogeneously.

Manufacturing of Lightweight Artificial Aggregate
The mixing proportions of artificial aggregate are shown in Table 3. For each of the mixes, character P denoted POFA, and S denoted silt. P0S10 was the control mix, which fully utilised silt without POFA. P1S9 was mixed with 10% POFA and 90% silt. There was a 10% interval increment for POFA up to 60%, which represented P6S4, based on the preliminary work. There were, in total, seven mixes in this study. The alkaline activator was prepared 1 day before mixing to ensure the homogeneous mixing of the materials. These series were designed to determine the properties of artificial aggregate by varying the proportion of POFA from 0% to 60%. The mixture of Na2O/SiO2 in a molar ratio of 2.5 was added to POFA and lime to act as the cementitious material for silt to produce artificial aggregate. The applied optimised parameter for artificial LWA production is summarised in Table 4. Table 4. Parameters used in the production of artificial LWA.

Manufacturing of Lightweight Artificial Aggregate
The mixing proportions of artificial aggregate are shown in Table 3. For each of the mixes, character P denoted POFA, and S denoted silt. P0S10 was the control mix, which fully utilised silt without POFA. P1S9 was mixed with 10% POFA and 90% silt. There was a 10% interval increment for POFA up to 60%, which represented P6S4, based on the preliminary work. There were, in total, seven mixes in this study. The alkaline activator was prepared 1 day before mixing to ensure the homogeneous mixing of the materials. These series were designed to determine the properties of artificial aggregate by varying the proportion of POFA from 0% to 60%. The mixture of Na 2 O/SiO 2 in a molar ratio of 2.5 was added to POFA and lime to act as the cementitious material for silt to produce artificial aggregate. The applied optimised parameter for artificial LWA production is summarised in Table 4. Table 4. Parameters used in the production of artificial LWA.

Parameters Description
Liquid to solid ratio, L/S 0.6 Alkaline activator ratio, Na 2 SiO 3 /NaOH 2.5 Lime content (% binder weight) 10 Water for silt (% silt weight) 69.2 Curing regime Room temperature (24 ± 2 h), followed by oven curing at 75 • C (24 ± 2 h) Sintering regime Preheating to 400 • C (20 min), followed by sintering at 1150 • C (1 h) Figure 3 illustrates the manufacturing procedures for artificial LWA. First, the POFA, alkaline activator, and CaO were mixed based on the optimal proportion, which was previously determined in a preliminary experiment. Wet silt was prepared according to the controlled amount of water derived from the plastic limit, and mixed with POFA to ensure the elasticity of the mixture for extrusion. The wet mixture was then extruded using an extruder, cut into a cylinder of approximately 8 mm in length, and rounded into a round spherical granular particle of 10 mm diameter with a modified granulation instrument. The granulation was 1-2 min per cycle. The fresh granular samples were placed in room temperature for 1 day to allow for a homogeneity reaction and then oven-dried for an additional day before sintering. This procedure was conducted to prevent rapid drying and defects in the microstructure of the pellets [21][22][23]. The sintering temperature and dwelling time were based on the preliminary experiment. The pellets were preheated to 400 • C for 20 min and sintered at 1150 • C for 1 h. This process was established to avoid bursting due to excessive rapid heating [15]. Thereafter, the sintered pellets were cooled at room temperature before testing.
x FOR PEER REVIEW 7 of 21 truded using an extruder, cut into a cylinder of approximately 8 mm in length, and rounded into a round spherical granular particle of 10 mm diameter with a modified granulation instrument. The granulation was 1-2 min per cycle. The fresh granular samples were placed in room temperature for 1 day to allow for a homogeneity reaction and then oven-dried for an additional day before sintering. This procedure was conducted to prevent rapid drying and defects in the microstructure of the pellets [21][22][23]. The sintering temperature and dwelling time were based on the preliminary experiment. The pellets were preheated to 400 °C for 20 min and sintered at 1150 °C for 1 h. This process was established to avoid bursting due to excessive rapid heating [15]. Thereafter, the sintered pellets were cooled at room temperature before testing.

Physical Properties
As shown in Figure 4, the artificial LWAs were within 1.2 g/cm 3 and were thus categorised as LWA. The bulk density of artificial LWA increased as the proportion of acti-

Physical Properties
As shown in Figure 4, the artificial LWAs were within 1.2 g/cm 3 and were thus categorised as LWA. The bulk density of artificial LWA increased as the proportion of activated POFA increased, and the silt content decreased. The bulk density values were within the range of 1.11-1.18 g/cm 3 . The specific gravity of raw material also affected the bulk density but only slightly after the sintering. During the sintering process, the bloating index (BI) increased, which gradually decreased the grain size and the bulk density of artificial LWA [30]. The density increased, while the BI increased. This result was due to the chemical composition of artificial LWA. Specifically, some of the mineralogy substances filled the expanded void during the sintering process, which increased the bulk density.  The dry specific gravity of artificial LWA generally should be less than 2.0 g/cm 3 , as per BS EN 13055-1-05 [30]. The specific gravity of the POFA-silt artificial aggregate in this study was 1.40-1.66 g/cm 3 , as shown in Figure 5. Therefore, this material could be classified as LWA. The specific gravity and bulk density of the artificial LWA substantially changed with the increases in activated POFA and binder. Samples P0S10 to P6S4 showed an increasing trend of dry density. Sample P6S4 obtained the highest density (1.66 g/cm 3 ), compared with the others. This was due to the high POFA content, which caused the sample to start to melt during the sintering process. The liquid phase filled the void presence within the artificial aggregate and thus increased the aggregate density. Thus, a dense crystalline with an outer layer that had a glassy texture was generated, given that the mixture was partially melted at the sintering temperature. Therefore, these retained particles within the artificial LWA formed a closed pore structure for the interstitial voids, which led to a low water absorption and high specific gravity. Moreover, the insulated outer layer limited the accessibility of water for artificial LWA. Sample P0S10 obtained a lower dry particle density at the same sintering temperature. This low density may have been caused by the bloating phenomenon during the sintering process, which resulted in an insufficient gas evolution to form pores within the fully silt pellets. The particle density measurement showed the effect of the binder, given that the proportion of POFA to silt for artificial LWA mixtures exhibited a rising trend in terms of density. The dry particle density increased as the activated POFA content increased. As the fineness of raw materials increased, the specific gravity of manufactured artificial aggregate increased.  The dry specific gravity of artificial LWA generally should be less than 2.0 g/cm 3 , as per BS EN 13055-1-05 [30]. The specific gravity of the POFA-silt artificial aggregate in this study was 1.40-1.66 g/cm 3 , as shown in Figure 5. Therefore, this material could be classified as LWA. The specific gravity and bulk density of the artificial LWA substantially changed with the increases in activated POFA and binder. Samples P0S10 to P6S4 showed an increasing trend of dry density. Sample P6S4 obtained the highest density (1.66 g/cm 3 ), compared with the others. This was due to the high POFA content, which caused the sample to start to melt during the sintering process. The liquid phase filled the void presence within the artificial aggregate and thus increased the aggregate density. Thus, a dense crystalline with an outer layer that had a glassy texture was generated, given that the mixture was partially melted at the sintering temperature. Therefore, these retained particles within the artificial LWA formed a closed pore structure for the interstitial voids, which led to a low water absorption and high specific gravity. Moreover, the insulated outer layer limited the accessibility of water for artificial LWA. Sample P0S10 obtained a lower dry particle density at the same sintering temperature. This low density may have been caused by the bloating phenomenon during the sintering process, which resulted in an insufficient gas evolution to form pores within the fully silt pellets. The particle density measurement showed the effect of the binder, given that the proportion of POFA to silt for artificial LWA mixtures exhibited a rising trend in terms of density. The dry particle density increased as the activated POFA content increased. As the fineness of raw materials increased, the specific gravity of manufactured artificial aggregate increased.  Figure 5 shows the water absorption of artificial LWA, with values of 13.10%, 13.23%, 13.46%, 11.70%, 11.75%, 9.81%, and 5.59%, which were within the acceptable range for concrete applications. The water absorption of LWA should not be more than 20% to ensure that the mechanical properties of the aggregate are suitable for concrete production [31,32]. The water absorption, which was below 10%, indicates that the surface of the manufactured LWA was well vitrified, as per standard 10262, 2009. Since the mixes had a high SiO2 content, this allowed for vitrification and a reduction in the water absorption of the aggregate. All of the produced artificial LWAs were within the acceptable limit in terms of water absorption ability, according to the standard. The POFA content level positively influenced the viscosity, which made the surface vitrified. Samples P0S10, P1S9, and P2S8 had high water absorption levels. This result was due to the low isolated surface, with more open pores on the surface, which increased the absorption rate. At 1150 °C, the water absorption decreased as the POFA content increased. This result was due to the formation of the glassy texture on the surface of artificial LWA. Therefore, the amount of water absorption for porous artificial LWA was lessened. The water absorption for sintered artificial LWA depended on the formation of a porous surface and glassy texture in the mixture. Sintered LWA had isolated open pores to limit the access of water through it. The sample with isolated pores and a vitrified matrix surface had a reduced absorption ability. Sample P6S4, with 60% activated POFA, had a low water absorption capacity (5.59%). It had an effective impermeable function, allowing the water to access the aggregate. The reduction in the accessibility of water through the surface connected to the interior porosity was due to its vitrified surface, with a glassy film. The dense external shell and impervious surface of P6S4 resulted in a reduction in the water absorption rate because the pores were sealed by the glassy phase.
By contrast, the sample with an open pore volume tended to absorb more water, given that it was affected by the open pore volume on the external surface [4]. Thus, the water absorption of the artificial LWA was not fully revealed through the SEM microstructure (interior pore size and number). If the open pore volume on the exterior surface area was lower, the water absorption rate was low, but the core region was porous. The analysis of the external surface showed that a cohesion of surface particles occurred.
However, more open pores were left on the shell surface if a viscous layer with a lower viscosity existed to allow more gases to escape. With the addition of CaO, the water ab-  Figure 5 shows the water absorption of artificial LWA, with values of 13.10%, 13.23%, 13.46%, 11.70%, 11.75%, 9.81%, and 5.59%, which were within the acceptable range for concrete applications. The water absorption of LWA should not be more than 20% to ensure that the mechanical properties of the aggregate are suitable for concrete production [31,32]. The water absorption, which was below 10%, indicates that the surface of the manufactured LWA was well vitrified, as per standard 10262, 2009. Since the mixes had a high SiO 2 content, this allowed for vitrification and a reduction in the water absorption of the aggregate. All of the produced artificial LWAs were within the acceptable limit in terms of water absorption ability, according to the standard. The POFA content level positively influenced the viscosity, which made the surface vitrified. Samples P0S10, P1S9, and P2S8 had high water absorption levels. This result was due to the low isolated surface, with more open pores on the surface, which increased the absorption rate. At 1150 • C, the water absorption decreased as the POFA content increased. This result was due to the formation of the glassy texture on the surface of artificial LWA. Therefore, the amount of water absorption for porous artificial LWA was lessened. The water absorption for sintered artificial LWA depended on the formation of a porous surface and glassy texture in the mixture. Sintered LWA had isolated open pores to limit the access of water through it. The sample with isolated pores and a vitrified matrix surface had a reduced absorption ability. Sample P6S4, with 60% activated POFA, had a low water absorption capacity (5.59%). It had an effective impermeable function, allowing the water to access the aggregate. The reduction in the accessibility of water through the surface connected to the interior porosity was due to its vitrified surface, with a glassy film. The dense external shell and impervious surface of P6S4 resulted in a reduction in the water absorption rate because the pores were sealed by the glassy phase.
By contrast, the sample with an open pore volume tended to absorb more water, given that it was affected by the open pore volume on the external surface [4]. Thus, the water absorption of the artificial LWA was not fully revealed through the SEM microstructure (interior pore size and number). If the open pore volume on the exterior surface area was lower, the water absorption rate was low, but the core region was porous. The analysis of the external surface showed that a cohesion of surface particles occurred. However, more open pores were left on the shell surface if a viscous layer with a lower viscosity existed to allow more gases to escape. With the addition of CaO, the water absorption for artificial LWA significantly decreased. The lime present on the geopolymer POFA reduced the percentage of water absorption. Figure 6 shows the void percentage for the artificial LWA. An increasing trend in the void percentage was observed for samples P0S10 to P5S5. The void percentage indicated the change in porosity or pores, which led to the change in density. The void percentage increased as the portion of activated POFA increased. The viscosity of the highly activated POFA sample mixture increased at the same sintering temperature. This was due to the occurrence of bloating behaviour within the artificial LWA. The microstructure of the samples also contributed to this effect, given that more voids formed from the fusion of particles.
Sustainability 2021, 13, x FOR PEER REVIEW 10 of 21 sorption for artificial LWA significantly decreased. The lime present on the geopolymer POFA reduced the percentage of water absorption. Figure 6 shows the void percentage for the artificial LWA. An increasing trend in the void percentage was observed for samples P0S10 to P5S5. The void percentage indicated the change in porosity or pores, which led to the change in density. The void percentage increased as the portion of activated POFA increased. The viscosity of the highly activated POFA sample mixture increased at the same sintering temperature. This was due to the occurrence of bloating behaviour within the artificial LWA. The microstructure of the samples also contributed to this effect, given that more voids formed from the fusion of particles.

Ignition Loss and BI
In this work, the weight loss percentage of artificial aggregate, before and after sintering, was known as the ignition loss of artificial aggregate. In the process of sintering, the weight loss was most probably due to the evaporation of the water content within the aggregate, the decomposition of the inorganic salt present in the mixture materials, and the emission or oxidation of the organic substances. The presence of highly powdered metallic aluminium encouraged the formation of an aluminium hydroxide Al(OH)3 gel with water, which was revealed by the mass loss of the aggregate. However, the formation of Al(OH)3 caused swelling. Therefore, the crack and fractures in the hardened aggregate could be prevented during preheating in the sintering process.
The LOI of the artificial LWA is shown in Figure 7. Sample P0S10 had a low LOI. Silt is rich in SiO2 and low in CaO. Thus, the fully silt artificial LWA was less porous and harder to vitrify at the desirable sintering temperature. The low LOI value resulted in less void formation within the artificial LWA. The convection of the elements within silt occurred when the relevant temperature was reached. A vitrified matrix was not formed for sample P0S10. Thus, the released gas escaped, instead of being trapped within the aggregate. The presence of POFA contributed to the increasing trend of LOI. The size of the artificial LWA also reduced as the BI decreased. When the activated POFA increased, the internal and external parts of the artificial LWA were glassy. Sample P6S4 showed a slight decrease in LOI. The reason was that the released gas was trapped within the vitrified surface of the aggregate, and the presence of melted particles filled the interior voids during the sintering process.

Ignition Loss and BI
In this work, the weight loss percentage of artificial aggregate, before and after sintering, was known as the ignition loss of artificial aggregate. In the process of sintering, the weight loss was most probably due to the evaporation of the water content within the aggregate, the decomposition of the inorganic salt present in the mixture materials, and the emission or oxidation of the organic substances. The presence of highly powdered metallic aluminium encouraged the formation of an aluminium hydroxide Al(OH) 3 gel with water, which was revealed by the mass loss of the aggregate. However, the formation of Al(OH) 3 caused swelling. Therefore, the crack and fractures in the hardened aggregate could be prevented during preheating in the sintering process.
The LOI of the artificial LWA is shown in Figure 7. Sample P0S10 had a low LOI. Silt is rich in SiO 2 and low in CaO. Thus, the fully silt artificial LWA was less porous and harder to vitrify at the desirable sintering temperature. The low LOI value resulted in less void formation within the artificial LWA. The convection of the elements within silt occurred when the relevant temperature was reached. A vitrified matrix was not formed for sample P0S10. Thus, the released gas escaped, instead of being trapped within the aggregate. The presence of POFA contributed to the increasing trend of LOI. The size of the artificial LWA also reduced as the BI decreased. When the activated POFA increased, the internal and external parts of the artificial LWA were glassy. Sample P6S4 showed a slight decrease in LOI. The reason was that the released gas was trapped within the vitrified surface of the aggregate, and the presence of melted particles filled the interior voids during the sintering process. The density loss of the artificial aggregate is related to the amount of gas that escaped during the sintering process. In this study, the bloating behaviour did not necessarily reflect the release of gas into atmosphere. This phenomenon was due to the influence of released gas after the formation of a viscous layer, as mentioned before. The results in this study evidenced that some of the generated gas for viscous layer formation escaped into the atmosphere and formed tiny pores without effective bloating for artificial LWA. The viscous glass phase was produced simultaneously to encapsulate the released gases, which contributed to the formation of an internal micro-pore structure. Figure 8 shows that all mixes of artificial LWA were classified as expanded aggregates, given that the BI was more than 1. The bloating behaviour was based on the chemical composition of the raw material to form a glassy phase by wrapping gas or the gas generated in the glassy phase [17]. Some samples had a high BI, because more gases were generated and trapped by the viscous melt as the sintering temperature reached 1150 °C. Different proportions of raw materials in the mixture induced changes in the BI. The high content of chemical composition (within the expansion area in the Riley ternary diagram) allowed the materials to expand and trap the released gas. The sintering temperature, released gas, and plastic phase, with the appropriate viscosity to trap the released gases, were run simultaneously [33]. The BI result, illustrated in Figure 8, showed the effect of raw materials on the degree of BI. As the proportion of POFA increased, the BI decreased. The reason was the occurrence of vitrification, which made the structure within the artificial LWA dense. This finding was supported by the study of González-Corrochano et. al. [34], which indicated that the raw materials affect the vitrification and mechanical performance of aggregate. The density loss of the artificial aggregate is related to the amount of gas that escaped during the sintering process. In this study, the bloating behaviour did not necessarily reflect the release of gas into atmosphere. This phenomenon was due to the influence of released gas after the formation of a viscous layer, as mentioned before. The results in this study evidenced that some of the generated gas for viscous layer formation escaped into the atmosphere and formed tiny pores without effective bloating for artificial LWA. The viscous glass phase was produced simultaneously to encapsulate the released gases, which contributed to the formation of an internal micro-pore structure. Figure 8 shows that all mixes of artificial LWA were classified as expanded aggregates, given that the BI was more than 1. The bloating behaviour was based on the chemical composition of the raw material to form a glassy phase by wrapping gas or the gas generated in the glassy phase [17]. Some samples had a high BI, because more gases were generated and trapped by the viscous melt as the sintering temperature reached 1150 • C. Different proportions of raw materials in the mixture induced changes in the BI. The high content of chemical composition (within the expansion area in the Riley ternary diagram) allowed the materials to expand and trap the released gas. The sintering temperature, released gas, and plastic phase, with the appropriate viscosity to trap the released gases, were run simultaneously [33]. The BI result, illustrated in Figure 8, showed the effect of raw materials on the degree of BI. As the proportion of POFA increased, the BI decreased. The reason was the occurrence of vitrification, which made the structure within the artificial LWA dense. This finding was supported by the study of González-Corrochano et al. [34], which indicated that the raw materials affect the vitrification and mechanical performance of aggregate.
The water absorption of artificial LWA remarkably dropped as the BI increased [28]. This result was due to the formation of a glassy external layer in the pellets, which drastically reduced the permeability of the LWA. The result in Figure 8 showed that the BI and water absorption were correlated with each other. Sample P0S10 had a BI of 2.88, and the BI was 4.43 for sample P6S4. The water absorption exhibited a declining trend from 13.10% (sample P0S10) to 5.59% (sample P6S4). The artificial LWA sintered under a high temperature involved a thermal shock to form a viscous mineral matrix for trapping the formation of evolved gases [35]. At a sintering temperature of 1150 • C, the sufficiently high temperature allowed the surface of the artificial LWA to be vitrified and envelop the emitted gas. The water absorption of artificial LWA remarkably dropped as the BI increased [28]. This result was due to the formation of a glassy external layer in the pellets, which drastically reduced the permeability of the LWA. The result in Figure 8 showed that the BI and water absorption were correlated with each other. Sample P0S10 had a BI of 2.88, and the BI was 4.43 for sample P6S4. The water absorption exhibited a declining trend from 13.10% (sample P0S10) to 5.59% (sample P6S4). The artificial LWA sintered under a high temperature involved a thermal shock to form a viscous mineral matrix for trapping the formation of evolved gases [35]. At a sintering temperature of 1150 °C, the sufficiently high temperature allowed the surface of the artificial LWA to be vitrified and envelop the emitted gas.
The activated POFA containing Na2O exhibited a high BI. This result could be explained by the low melting point in the presence of Na2O at the sintering temperature [32] and as the proportion of the activated POFA increased. Therefore, this phenomenon could lead to a rapid sintering reaction. As for the proportion of activated POFA up to 70%, the sample was melted in the pre-experiment. The high proportion of activated POFA increased the viscosity and thus encapsulate the bloating gases.
The presence of Fe2O3 in the aggregate decomposed during the sintering process and liberated gases (O2 or SO2). These released gases probably reacted with the unburned carbon content in the activated POFA to form carbon oxide. A sintering temperature above 1050 °C promoted the generation of liquid and crystal phases. The chemical compositions of SiO2 and Al2O3 that controlled the viscosity of artificial LWA at high temperatures determined the crystalline quality and the crystallisation rate. Thus, the properties of artificial LWA were affected by the chemical oxide in the sintering process [36].

Mechanical Properties
The effect on the crushing strength of artificial aggregate was due to the different mix proportions of the POFA to silt. The average results of each series of samples at 7, 14, 28, 56, and 90 days are shown in Figure 9. The overall trend observed from the results showed that the ultimate strength achieved by P4S6 was 5.43 MPa at 28 days of curing. As expected, the crushing strength of artificial LWA increased as the binder content in- The activated POFA containing Na 2 O exhibited a high BI. This result could be explained by the low melting point in the presence of Na 2 O at the sintering temperature [32] and as the proportion of the activated POFA increased. Therefore, this phenomenon could lead to a rapid sintering reaction. As for the proportion of activated POFA up to 70%, the sample was melted in the pre-experiment. The high proportion of activated POFA increased the viscosity and thus encapsulate the bloating gases.
The presence of Fe 2 O 3 in the aggregate decomposed during the sintering process and liberated gases (O 2 or SO 2 ). These released gases probably reacted with the unburned carbon content in the activated POFA to form carbon oxide. A sintering temperature above 1050 • C promoted the generation of liquid and crystal phases. The chemical compositions of SiO 2 and Al 2 O 3 that controlled the viscosity of artificial LWA at high temperatures determined the crystalline quality and the crystallisation rate. Thus, the properties of artificial LWA were affected by the chemical oxide in the sintering process [36].

Mechanical Properties
The effect on the crushing strength of artificial aggregate was due to the different mix proportions of the POFA to silt. The average results of each series of samples at 7, 14, 28, 56, and 90 days are shown in Figure 9. The overall trend observed from the results showed that the ultimate strength achieved by P4S6 was 5.43 MPa at 28 days of curing. As expected, the crushing strength of artificial LWA increased as the binder content increased. However, the crushing strength decreased when the POFA content was beyond 50% of the weight. This phenomenon could be due to the activator POFA, which resulted in the formation of a vitrified structure. The fully silt artificial LWA P0S10 exhibited 3.74 MPa at 28 days. This result was due to the silt failing to boost the crushing strength or enhancing the viscosity without a supporting binder. The crushing strength was also correlated with the BI and density. Whether the formation of the microstructure could withstand the resistance was unclear. A decreasing trend was observed for samples P5S5 and P6S4, which did not explain why the great vitrification enhanced the strength of the aggregate. This result could be explained by the fact that the chemical composition affected the crushing strength of the artificial LWA due to the lower resistance of the internal microstructure. The minimum crushing value (3.7MPa) was 69% of the maximum value (5.4 MPa). Therefore, properties apart from the density, water absorption, morphology of hydration products, and resulting microstructure would also strongly affect the mechanical performance of the artificial LWA. The increase in the activated POFA content modified the densification behaviour of the mixture, which changed the softening point and sintering temperature with the change in the chemical composition and mineralogy of the mixture. The commercially available LWA has a density of 1.485, a water absorption of 15.5%, and a crushing strength value of 6.9 MPa [37]. Therefore, the crushing strength of the artificial LWA was affected by some interrelated factors, including the density value, shape, size dimension, texture, water absorption (pore distribution and size), BI, and densification of the aggregate. correlated with the BI and density. Whether the formation of the microstructure could withstand the resistance was unclear. A decreasing trend was observed for samples P5S5 and P6S4, which did not explain why the great vitrification enhanced the strength of the aggregate. This result could be explained by the fact that the chemical composition affected the crushing strength of the artificial LWA due to the lower resistance of the internal microstructure. The minimum crushing value (3.7MPa) was 69% of the maximum value (5.4 MPa). Therefore, properties apart from the density, water absorption, morphology of hydration products, and resulting microstructure would also strongly affect the mechanical performance of the artificial LWA. The increase in the activated POFA content modified the densification behaviour of the mixture, which changed the softening point and sintering temperature with the change in the chemical composition and mineralogy of the mixture. The commercially available LWA has a density of 1.485, a water absorption of 15.5%, and a crushing strength value of 6.9 MPa [37]. Therefore, the crushing strength of the artificial LWA was affected by some interrelated factors, including the density value, shape, size dimension, texture, water absorption (pore distribution and size), BI, and densification of the aggregate. In general, the artificial LWA with more pores resulted in a low crushing strength. In this study, a good strength was observed for sample P4S6. The reason might be that the formation of pores within the interior of the LWA was closed (not fused) and had a relatively consistent distribution. In addition, the presence of a glassy phase contributed to the crushing strength due to the presence of silicate glass and calcium silicate on the external layer. The appearance, such as the texture of the artificial LWA and pore volume, might affect the bond strength within the cement-aggregate phase. However, the effect would be evident in the early stage of the curing. Thus, the effect in the later stage would be less significant due to the formation of a strong chemical bond.
A good correlation exists between the crushing and impact value for artificial LWA, which can be used to determine the performance of the aggregate. In general, the crushing and impact value provide a full understanding of the strength of the artificial LWA. A high percentage of the impact value indicates that the aggregate has a lower resistance to In general, the artificial LWA with more pores resulted in a low crushing strength. In this study, a good strength was observed for sample P4S6. The reason might be that the formation of pores within the interior of the LWA was closed (not fused) and had a relatively consistent distribution. In addition, the presence of a glassy phase contributed to the crushing strength due to the presence of silicate glass and calcium silicate on the external layer. The appearance, such as the texture of the artificial LWA and pore volume, might affect the bond strength within the cement-aggregate phase. However, the effect would be evident in the early stage of the curing. Thus, the effect in the later stage would be less significant due to the formation of a strong chemical bond.
A good correlation exists between the crushing and impact value for artificial LWA, which can be used to determine the performance of the aggregate. In general, the crushing and impact value provide a full understanding of the strength of the artificial LWA. A high percentage of the impact value indicates that the aggregate has a lower resistance to sudden impacts. The results for each of the samples are presented in Figure 10. As observed, the impact resistance improved as the activated POFA ratio increased. This finding was due to the enhancement in the cement-aggregate bond as a result of the C-S-H formation. The further reaction of the chemical compound in silt and CaO in activated POFA increased the strength. Sample P4S6 had an impact resistance of 24.9%. Samples P5S5 and P6S4 had a slight increment. This result might be because the excessively activated POFA made CaO abundant, which resulted in particles not being reacted because of the rapid hardening process. Samples P3S7 to P6S4 displayed an impact value positioned within the acceptable impact limit, as per BS-812-12. By contrast, the impact value of samples P0S10 to P2S8 did not fall within the impact limit after 28 days of curing. The analysis of the crushing strength and impact value showed that a dense matrix and low water absorption positively contributed to the mechanical performance of the artificial LWA.
P5S5 and P6S4 had a slight increment. This result might be because the excessively activated POFA made CaO abundant, which resulted in particles not being reacted because of the rapid hardening process. Samples P3S7 to P6S4 displayed an impact value positioned within the acceptable impact limit, as per BS-812-12. By contrast, the impact value of samples P0S10 to P2S8 did not fall within the impact limit after 28 days of curing. The analysis of the crushing strength and impact value showed that a dense matrix and low water absorption positively contributed to the mechanical performance of the artificial LWA. The chemical soundness of the artificial LWA was determined according to the standard IS 2386-Part 5 to investigate the resistance of artificial LWA under a magnesium sulphate solution (assumed weathering condition) [38]. The method to run this test was stated in the previous section. The loss of soundness was interrelated to the absorption. The result showed that sample P0S10 had a 4.1% weight reduction, and the value was 0.2% for sample P6S4. The remaining samples obtained 2.5%, 1.1%, 0.9%, 0.7%, and 0.5%. The values of all the samples fell within the limit range of less than 12%, as recommended in ASTM C-88 [39]. Therefore, the samples of artificial LWA had an acceptable loss of soundness to resist changes in volume under the subjected condition.

The SEM Microstructure of Artificial Aggregate
The microstructures of the internal section of the artificial LWA at varying proportions of POFA-silt were determined by SEM. The dry particle density, water absorption, and crushing strength could be correlated with the microstructure of the artificial LWA. The internal microstructure of LWA was nearly similar for those within the strength range, even with different raw materials or production methods [34]. The artificial LWA showed a dense matrix that contained a significant volume of isolated pores, as the activated POFA content increased. The pore size and void arrangement were affected by the proportion of the mixture for artificial aggregate production. This formation occurred due to the vapor evaporation, oxidation of organic substances, and de-carbonation dur- The chemical soundness of the artificial LWA was determined according to the standard IS 2386-Part 5 to investigate the resistance of artificial LWA under a magnesium sulphate solution (assumed weathering condition) [38]. The method to run this test was stated in the previous section. The loss of soundness was interrelated to the absorption. The result showed that sample P0S10 had a 4.1% weight reduction, and the value was 0.2% for sample P6S4. The remaining samples obtained 2.5%, 1.1%, 0.9%, 0.7%, and 0.5%. The values of all the samples fell within the limit range of less than 12%, as recommended in ASTM C-88 [39]. Therefore, the samples of artificial LWA had an acceptable loss of soundness to resist changes in volume under the subjected condition.

The SEM Microstructure of Artificial Aggregate
The microstructures of the internal section of the artificial LWA at varying proportions of POFA-silt were determined by SEM. The dry particle density, water absorption, and crushing strength could be correlated with the microstructure of the artificial LWA. The internal microstructure of LWA was nearly similar for those within the strength range, even with different raw materials or production methods [34]. The artificial LWA showed a dense matrix that contained a significant volume of isolated pores, as the activated POFA content increased. The pore size and void arrangement were affected by the proportion of the mixture for artificial aggregate production. This formation occurred due to the vapor evaporation, oxidation of organic substances, and de-carbonation during the sintering process, and it depended on the mix proportion for artificial LWA production. Figure 11 shows the change in the microstructure of samples with different proportions at the sintering temperature. Condensed pores, vitrified layers, isolated pores, enlarged pores, or coating melts were formed in the outer and interior parts of the artificial LWA. The SEM morphology of samples a (P0S10) and b (P1S9) showed a nearly similar structure with abundant small voids and a few large pores. No glassy layer was formed in the core fragment morphology. Thus, sample a (P0S10) failed to trap the expanded gas. Sample a (P0S10) had fewer and finer pores in the fractured core. The pores were not interconnected and did not expand. This sample also had a glossy and smooth inner pore surface. The interior of the samples appeared to be not fully vitrified/bloating. This result was due to the gas causing decomposition reactions in a glassy matrix of a low viscosity. The sample with a low water absorption consisted of closed pores inside the compound matrix. The microparticles of b (P1S9) started to slightly expand, but the expansion was limited. was easily detected in the microstructure image. The sample with 70% POFA melted at the sintering temperature of 1150 °C. This phenomenon occurred because the chemical composition of the aggregate mixture reached its melting point.
The presence of lime in POFA acted as a stabiliser with silt and further reacted with the silicate in POFA and silt to form a stronger binder or cement of the calcium silicate and aluminate hydrate. This substance was produced when the hydration process was formed.

X-ray Diffraction of Artificial Aggregate
The X-ray diffraction (XRD) analysis results are shown in Figure 12. The major crystalline phase presence is quartz (SiO2) for all the samples, where the artificial LWA exhibited an amorphous characteristic. The property of raw material for the artificial aggregate production contributed to the major prominent oxide, since it contained a high SiO2 content. For sample P0S10, the crystalline phases performed included quartz, illite, microcline, and muscovite. Sample P1S9 consisted of quartz, cristobalite, diopside, and jacobsite. The mullite present had a low coefficient of the thermal expansion, which allowed for less expanded gas to form in the artificial LWA. The crystalline phases of quartz, oligoclase, hermatile, titanomagnetite, and manganese were found in sample P2S8. FeO was not observed, since there was no wuestite phase in the XRD pattern. Moreover, sample P3S7 illustrated quartz, oligoclase, hermatile, magnesioferrite, and kyanite. Kyanite is an anhydrous aluminosilicate, and it is detected at 1150 °C sintering for aggregate samples with more than 30% POFA. The presence of kyanite contributed to the compressive strength, as it compromised the crushing strength for artificial LWA. The mineral phase present in sample P5S5 was almost similar to that of sample P4S6. Sample P4S6 had crystalline phases of quartz, oligoclase, siderite, and kyanite. With the incorporation of activated POFA, the C-S-H formation was enhanced, which was in As the proportion of activated POFA increased, the pores eventually expanded due to the low viscosity to withstand the bloating force from the released gas. This internally generated an isolated void, followed by a softened phenomenon. The enlargement of pores was attributed to the vapor entrapment derived from the generated gas from the viscous composition within the artificial LWA. An obvious volatilisation was observed in sample d (P3S7) to f (P5S5). The artificial LWA started to develop a glassy layer, with a notable void formation. When the proportion of POFA content increased, a large void existed and was surrounded by a glassy layer. The raw POFA contained higher CaO and MgO contents than silt. Thus, the sintering temperature stimulated a sudden change in viscosity. The formation of large pores was followed by a glassy phase. Sample g (P6S4) gained the external glassy film, which resulted in a low water absorption. The continuous viscous phase during the sintering process decreased or broke the void to form an interconnection within the aggregate and thus affected the strength of the artificial LWA. Therefore, the higher amount of isolated spherical pores in the fractured cores and the thicker inter-pore crystalline phases affected the artificial LWA with a high activated POFA content. For sample g (P6S4), the formation of the large void was distorted without the glassy wall. The viscosity to capture the expanded gas was limited, and the sample was nearly or partially melted. The bloating effect and fusing occurred in the activated POFA at 1150 • C. As the ratio of activated POFA increased, the portion to be expanded was easily detected in the microstructure image. The sample with 70% POFA melted at the sintering temperature of 1150 • C. This phenomenon occurred because the chemical composition of the aggregate mixture reached its melting point.
The presence of lime in POFA acted as a stabiliser with silt and further reacted with the silicate in POFA and silt to form a stronger binder or cement of the calcium silicate and aluminate hydrate. This substance was produced when the hydration process was formed.

X-ray Diffraction of Artificial Aggregate
The X-ray diffraction (XRD) analysis results are shown in Figure 12. The major crystalline phase presence is quartz (SiO 2 ) for all the samples, where the artificial LWA exhibited an amorphous characteristic. The property of raw material for the artificial aggregate production contributed to the major prominent oxide, since it contained a high SiO 2 content. For sample P0S10, the crystalline phases performed included quartz, illite, microcline, and muscovite. Sample P1S9 consisted of quartz, cristobalite, diopside, and jacobsite. The mullite present had a low coefficient of the thermal expansion, which allowed for less expanded gas to form in the artificial LWA. The crystalline phases of quartz, oligoclase, hermatile, titanomagnetite, and manganese were found in sample P2S8. FeO was not observed, since there was no wuestite phase in the XRD pattern. Moreover, sample P3S7 illustrated quartz, oligoclase, hermatile, magnesioferrite, and kyanite. Kyanite is an anhydrous aluminosilicate, and it is detected at 1150 • C sintering for aggregate samples with more than 30% POFA. The presence of kyanite contributed to the compressive strength, as it compromised the crushing strength for artificial LWA. The mineral phase present in sample P5S5 was almost similar to that of sample P4S6. Sample P4S6 had crystalline phases of quartz, oligoclase, siderite, and kyanite. With the incorporation of activated POFA, the C-S-H formation was enhanced, which was in agreement with the crushing strength. Sample P6S4 detected a rose in the quartz intensity due to the formation of a glassy phase during the sintering process.

Conclusions
The use of by-product residues of POFA and unwanted sludge as artificial LWA is not only useful in exploring alternatives to natural aggregate, but also provides a solution P5S5 P6S4 Figure 12. XRD of artificial LWA at various mix proportion ratios.

Conclusions
The use of by-product residues of POFA and unwanted sludge as artificial LWA is not only useful in exploring alternatives to natural aggregate, but also provides a solution for waste management through the recycling and reuse of wastes. The general properties of the raw materials show that it is highly likely that they can be used to generate artificial LWA. This study demonstrated that activated POFA-silt could be used to manufacture artificial LWA through the cementitious granulation of POFA geopolymer. The performance of the combination of sintered POFA-silt artificial LWA was evaluated. The results showed that alkaline-activated POFA with silt could be used for artificial LWA production. The physical, mechanical, and durability properties of artificial POFA-silt LWA sintered at 1150 • C were determined. The findings are as follows: (1) All of the mix proportions of artificial LWA were in accordance with the standard in terms of density and water absorption. Each of the artificial LWAs had different trends, which were all within the limit range. (2) The use of lime (CaO) in POFA produced a pozzolanic material through a chemical reaction with the silicate mineral in POFA. When it was combined with silt, a hydration process occurred due to the presence of CaOH, silicate, and aluminate in the silt, which caused a binder of calcium silicate or aluminate hydrate to form, thus enhancing the reaction in the artificial LWA. (3) Waste materials with high SiO 2 , Al 2 O 3 , and CaO contents, such as silt and POFA, had a high potential to be manufactured as artificial aggregates with the addition of additives, which is due to the formation of a C-S-H gel or Na-Al-H gel during the reaction. SiO 2 and Al 2 O 3 mainly controlled the viscosity of the glassy phase. These materials affected the properties of the artificial aggregates, such as their bulk density, particle density, and water absorption. (4) The bulk and particle densities of the artificial LWA were consistent with the requirement of LWA. Thus, all of the POFA-silt artificial aggregates were classified as LWA.
The water absorption of the artificial aggregates was considered acceptable. The reason was that a vitrified external layer formed in all samples, with a better ratio of activated POFA. (5) Sample P4S6 exhibited a satisfactory performance in the property tests. The physical properties fell within the requirement. It achieved the highest strength in terms of single aggregate crushing. Sample P4S6 was a good optimal mix proportion for artificial LWA production. This artificial LWA could be applied to concrete slabs and building structures. It could also be used for lightweight structures or insulation concrete to fulfil the need for high-strength and lightweight concrete. (6) The chemical mineralogy of the raw materials in different proportions for artificial LWA production affected the pore formation within the artificial LWA and the degree of vitrification. (7) The slightly abnormal performance of the artificial LWA might be due to the sintering process. The location of the aggregate induced changes in the texture, causing it to be either well vitrified or less vitrified. This phenomenon occurred because of the circulation of heat inside the furnace, which failed to completely reach each stationary artificial LWA.
This work could serve as a reference in material waste recycling or reuse and recovery. The developed material could be used as an alternative to address the overconsumption of natural aggregate. It could also be a feasible solution for industrial waste management. The artificial LWA could be manufactured in large amounts to reduce costs and energy consumption. Thus, further investigations could be conducted to explore more related possibilities, such as other potential geopolymer sources, the addition of admixture or superplasticiser, and more efficient production methods.