Evaluation of Mechanical and Environmental Properties of Engineered Alkali-Activated Green Mortar

Currently, alkali-activated binders using industrial wastes are considered an environmentally friendly alternative to ordinary Portland cement (OPC), which contributes to addressing the high levels of carbon dioxide (CO2) emissions and enlarging embodied energy (EE). Concretes produced from industrial wastes have shown promising environmentally-friendly features with appropriate strength and durability. From this perspective, the compressive strength (CS), CO2 emissions, and EE of four industrial powder waste materials, including fly ash (FA), palm oil fly ash (POFA), waste ceramic powder (WCP), and granulated blast-furnace slag (GBFS), were investigated as replacements for OPC. Forty-two engineered alkali-activated mix (AAM) designs with different percentages of the above-mentioned waste materials were experimentally investigated to evaluate the effect of each binder mass percentage on 28-day CS. Additionally, the effects of each industrial powder waste material on SiO2, CaO, and Al2O3 contents were investigated. The results confirm that adding FA to the samples caused a reduction of less than 26% in CS, whereas the replacement of GBFS by different levels of POFA significantly affected the compressive strength of specimens. The results also show that the AAM designs with a high volume FA provided the lowest EE and CO2 emission levels compared to other mix designs. Empirical equations were also proposed to estimate the CS, CO2 emissions, and EE of AAM designs according to their binder mass compositions.


Introduction
There is environmental concern worldwide regarding the production of OPC, as it is widely employed as a concrete binder in construction industries. It is commonly accepted that the manufacturing of OPC causes serious pollution issues, including a considerable amount of CO 2 emissions. It was estimated that around 10 billion metric tons of concrete are produced annually and that the majority of these products contain OPC [1]. Every tonne of OPC creates approximately one tonne of CO 2 ; it was estimated that almost 7% of all the CO 2 emissions produced globally are attributed to OPC production and its equivalent raw material extraction [2]. It was also estimated that the manufacturing of OPC will quadruple over the next three decades, which is expected to lead to extensive environmental, ecological, and economic degradation [3].
countries is continuously increasing [25]. POFA has no market value, and its application is normally limited to land filling in lagoons and ponds, which is a major environmental concern. Recent studies classified POFA as a pozzolanic substance that is rich in silica content [26]. Accordingly, such a cheap and abundantly available resource material can be used as a partial substitute for OPC or as an AAM binder to improve strength and durability.
ACIMAC, the association of Italian manufacturers of machinery and equipment for the ceramic industry, published a report indicating that around 13.7 billion m 2 ceramic tiles were produced in 2018 worldwide [27]. Around 30% of the products in this industry go to waste. Waste ceramics are significantly resistant and durable to harsh environmental conditions. To date, this waste material has mainly been recycled as a filler in tartan floors and gardening. As an effort toward sustainable design, several studies proposed the application of ceramic waste in concrete and mortar and concluded that such wastes significantly improved the workability of fresh mortars due to the excess amount of water absorption that occurred during the geopolymerization process [28][29][30]. Lu et al. [31] found that including fine ceramic aggregates (up to 50%) in a concrete mix design improved the concrete's durability performance and CS.
Several studies addressed the application of industrial waste materials in alkali-activated mix designs as a sustainable substitute for OPC [32][33][34]. Nevertheless, several issues, such as a reliable method to predict the mechanical behavior and optimum composition of the binder mass, did not receive enough attention, leading to a limit on their mass production. In this study, the 28-day CS of zero-OPC binder with ternary blended alkali-activated mix designs composed of industrial waste materials (FA, GBFS, POFA, and WCP) was investigated using experimental tests and scanning electron microscopy (SEM). Since the AAM designs are affected by the chemical composition of each industrial waste material, the effects of each material replacement on SiO 2 , CaO, and Al 2 O 3 contents were investigated in detail. The CO 2 emissions, and EE of all AAM designs with different binder mass constitutions were also investigated using a cradle-to-gate approach. Empirical equations were also proposed in this paper to estimate the CS, CO 2 emissions, and EE of AAM designs according to their binder mass compositions.

Wastes Material Characterization
Based on trial mixes, the optimum values of sodium hydroxide molarity, sodium silicate to sodium hydroxide ratio, alkaline solution to binder ratio, and binder to aggregate ratio were selected and these values were fixed for all cement-free AAM designs. Ternary blended contents using GBFS, FA and POFA, or WCP were examined to determine the influence of calcium oxide on the geopolymerization process. GBFS content as a source of CaO was kept to a minimum of 20% in the replacement process and a maximum of 70%. By using an X-ray fluorescence spectroscopy (XRF) test, the chemical compositions of the studied waste material were determined, as shown in Table 1. Table 1 reveals that the major compound in FA, WCP, and POFA is SiO 2 (57.2, 72.6, and 64.2%, respectively), whereas in GBFS, it is CaO (51.8%). Al 2 O 3 , SiO 2 , and CaO are essential oxides throughout the hydration process and production process of the C(A)SH gels. Nevertheless, the low contents of CaO and Al 2 O 3 in WCP require including materials comprising high quantities of CaO (GBFS) and Al 2 O 3 (FA) to produce high-performance alkali-activated binders. According to ASTM C618-15 [35], FA and WCP are classified as class F pozzolans as a result of the existence (higher than 70%) of SiO 2 + Al2O 3 + Fe 2 O 3 .
To prepare POFA and WCP industrial waste materials powder, the Loss Angelos Abrasion machine that operates with 15 stainless balls each of diameter 50 mm, drum speed in the range of 32-35 revolutions per minute (rpm) had been used. The duration of grinding influences the finesse of particles, which is monitored every one hour. In this research, the percentage of particles was retained at 45 µm.

Scanning Electron Microscope (SEM) Images
High-Resolution, magnified images in SEM are useful within materials science to test the quality of materials, ensuring that they are fit for purpose and can be used to predict and prevent material failure. SEM analyses were performed using a Hitachi SU8020 microscope with an Energy Dispersive Spectroscopy (EDS). SEM images of FA revealed that it is comprised of regular spherical particles, while GBFS is comprised of irregular angular particles, as shown in Figure 1.  Table 1 reveals that the major compound in FA, WCP, and POFA is SiO2 (57.2, 72.6, and 64.2%, respectively), whereas in GBFS, it is CaO (51.8%). Al2O3, SiO2, and CaO are essential oxides throughout the hydration process and production process of the C(A)SH gels. Nevertheless, the low contents of CaO and Al2O3 in WCP require including materials comprising high quantities of CaO (GBFS) and Al2O3 (FA) to produce high-performance alkali-activated binders. According to ASTM C618-15 [35], FA and WCP are classified as class F pozzolans as a result of the existence (higher than 70%) of SiO2 + Al2O3 + Fe2O3.
To prepare POFA and WCP industrial waste materials powder, the Loss Angelos Abrasion machine that operates with 15 stainless balls each of diameter 50 mm, drum speed in the range of 32-35 revolutions per minute (rpm) had been used. The duration of grinding influences the finesse of particles, which is monitored every one hour. In this research, the percentage of particles was retained at 45 μm.

Scanning Electron Microscope (SEM) Images
High-Resolution, magnified images in SEM are useful within materials science to test the quality of materials, ensuring that they are fit for purpose and can be used to predict and prevent material failure. SEM analyses were performed using a Hitachi SU8020 microscope with an Energy Dispersive Spectroscopy (EDS). SEM images of FA revealed that it is comprised of regular spherical particles, while GBFS is comprised of irregular angular particles, as shown in Figure 1. Recycled tile ceramic waste with the same thickness and no glassy coating was collected, resulting in homogeneous waste. The manufacturing process of WCP involved several steps, including (1) crushing ceramic tiles using a jaw crusher, (2) sieving with a 600 μm sieve to remove large particles, and (3) grinding using a Los Angeles abrasion machine for 6 h. To prepare POFA, large particles were first removed using a 600 μm sieve, which were then dried in an oven at 105 °C for 24 h. Subsequently, they were sieved using a 300 μm sieve and ground using a Los Angeles abrasion machine for 6 h to achieve fine particles. The SEM image of POFA clearly revealed the presence of irregular and spherical particles, whereas the SEM image of the ceramic waste indicated it contained irregular and angular particles, as shown in Figure 2. Recycled tile ceramic waste with the same thickness and no glassy coating was collected, resulting in homogeneous waste. The manufacturing process of WCP involved several steps, including (1) crushing ceramic tiles using a jaw crusher, (2) sieving with a 600 µm sieve to remove large particles, and (3) grinding using a Los Angeles abrasion machine for 6 h. To prepare POFA, large particles were first removed using a 600 µm sieve, which were then dried in an oven at 105 • C for 24 h. Subsequently, they were sieved using a 300 µm sieve and ground using a Los Angeles abrasion machine for 6 h to achieve fine particles. The SEM image of POFA clearly revealed the presence of irregular and spherical particles, whereas the SEM image of the ceramic waste indicated it contained irregular and angular particles, as shown in Figure 2.

Design of the Alkali-Activated Mix Designs
Based on trial mixes, the optimum values of sodium hydroxide molarity, sodium silicate to sodium hydroxide ratio, alkaline solution to binder ratio, and binder to fine aggregate ratio were selected as 4 M, 0.75, 0.40, and 1.0, respectively. These values were fixed for all alkali-activated mix designs. Additionally, all mixtures had a standard and fixed proportion of fine and course aggregate. Analytical-grade NaOH (NH, 98% purity) was purchased from QREC (Johor, Malaysia) as an alkali activator to prepare the proposed alkali-activated mortars. An analytical grade sodium silicate solution comprised of SiO2 (29.5 wt %), Na2O (14.70 wt %), and H2O (55.80 wt %) was procured from QREC (Johor, Malaysia). The NaOH pellets were dissolved in water to prepare the alkaline solution of 4 M concentration. The solution was first cooled for 24 h and then added to sodium silicate (NS) solution to obtain an alkaline solution with a SiO2 to Na2O ratio of 1.02. The ratio of NS to NH was fixed to 0.75 for all the alkaline mixtures. Overall, four distinct AAM designs with ternary blended contents using GBFS, FA, POFA, and WCP were examined to determine the influence of calcium oxide on the geopolymerization process and CS.

High Volume Fly Ash Mix Design
This section describes the effect of GBFS replacement by FA at various levels on the contents of SiO2, CaO, and Al2O3 in AAMs. Three levels of replacement were adopted to evaluate the effect of CaO on the geopolymerization process. At each level, the minimum content of GBFS was kept as low as 20%. At every level, the GBFS was replaced by POFA to evaluate the effect of increasing silica oxide and reducing aluminum oxide on AAM properties. Table 2 displays the effect of GBFS replaced by FA and POFA replaced by GBFS on SiO2, CaO, and Al2O3 contents. CaO content was observed to increase with increasing GBFS content and decreasing FA and POFA contents. CaO content increased from 19.2% to 23.8% and 28.5% with the replacement of FA by GBFS with 30%, 40%, and 50% portions, respectively. SiO2 content increased with the increase in POFA content. However, Al2O3 content decreased with increasing GBFS and POFA contents and decreasing FA content.

Design of the Alkali-Activated Mix Designs
Based on trial mixes, the optimum values of sodium hydroxide molarity, sodium silicate to sodium hydroxide ratio, alkaline solution to binder ratio, and binder to fine aggregate ratio were selected as 4 M, 0.75, 0.40, and 1.0, respectively. These values were fixed for all alkali-activated mix designs. Additionally, all mixtures had a standard and fixed proportion of fine and course aggregate. Analytical-grade NaOH (NH, 98% purity) was purchased from QREC (Johor, Malaysia) as an alkali activator to prepare the proposed alkali-activated mortars. An analytical grade sodium silicate solution comprised of SiO 2 (29.5 wt %), Na 2 O (14.70 wt %), and H 2 O (55.80 wt %) was procured from QREC (Johor, Malaysia). The NaOH pellets were dissolved in water to prepare the alkaline solution of 4 M concentration. The solution was first cooled for 24 h and then added to sodium silicate (NS) solution to obtain an alkaline solution with a SiO 2 to Na 2 O ratio of 1.02. The ratio of NS to NH was fixed to 0.75 for all the alkaline mixtures. Overall, four distinct AAM designs with ternary blended contents using GBFS, FA, POFA, and WCP were examined to determine the influence of calcium oxide on the geopolymerization process and CS.

High Volume Fly Ash Mix Design
This section describes the effect of GBFS replacement by FA at various levels on the contents of SiO 2 , CaO, and Al 2 O 3 in AAMs. Three levels of replacement were adopted to evaluate the effect of CaO on the geopolymerization process. At each level, the minimum content of GBFS was kept as low as 20%. At every level, the GBFS was replaced by POFA to evaluate the effect of increasing silica oxide and reducing aluminum oxide on AAM properties. Table 2 displays the effect of GBFS replaced by FA and POFA replaced by GBFS on SiO 2 , CaO, and Al 2 O 3 contents. CaO content was observed to increase with increasing GBFS content and decreasing FA and POFA contents. CaO content increased from 19.2% to 23.8% and 28.5% with the replacement of FA by GBFS with 30%, 40%, and 50% portions, respectively. SiO 2 content increased with the increase in POFA content. However, Al 2 O 3 content decreased with increasing GBFS and POFA contents and decreasing FA content. Nine mixtures were prepared to evaluate the high-volume content of POFA on the AAM properties, as shown in Table 3. The high level of POFA (70%) was reduced to 60% and 50% via the replacement by GBFS and FA. The GBFS content was kept between 20% and 50%. The results revealed that a reduction in the POFA content from 70% to 50% led to reducing the silicate content. The Al 2 O 3 content increased when the ratio of GBFS to FA increased, while the CaO content significantly declined.

High Volume GBFS Mix Design
To evaluate the effect of high CaO contents on the geopolymerization process and the properties of AAM designs, 15 mixes were synthesized. Three levels of GBFS content were prepared, with 50%, 60%, and 70%. Then, the GBFS was replaced by FA and POFA. Table 4 illustrates the effects of GBFS content on SiO 2 , CaO, and Al 2 O 3 contents. An increase in the GBFS content from 50% to 60% and 70% was observed to lead to an increase in CaO content from 28.5% to 33.2% and 37.8%, respectively. Additionally, SiO 2 content increased with the reduction in GBFS content and the increase in POFA content, whereas Al 2 O 3 content increased with increasing FA content.

High Volume Ceramic Waste Mix Design
The effect of CaO on activated blended content with a high amount of SiO 2 and Al 2 O 3 was considered in this mix design. Nine mixtures containing a high amount of ceramic waste were prepared. Three levels of ceramic waste were adopted, including 50%, 60%, and 70%, and replaced with GBFS and FA. The minimum content of GBFS was kept at 20% and the maximum was kept at 50%. The effect of the high volume of WCP and the ratio of GBFS to FA on the contents of SiO 2 , CaO, and Al 2 O 3 are shown in Table 5. An increase in the content of WCP led to an enhancement of SiO 2 content. The replacement of WCP by increasing the amount of GBFS led to an increase in the CaO content. Al 2 O 3 content also increased with increasing FA content.

Test Procedure
For the casting process, the resulting mortar was poured into the molds using the two-layers pouring method. In this process, each layer was subject to a vibration for a period of 15 s in order to eliminate any air pockets within the mixture. Once the casting process was completed, the AAMs were cured for 24 h in an ambient atmosphere (temperature 24 ± 1.5 • C, relative humidity 75%) before the demolding process. The compression strength of all specimens was measured at 28 days, following ASTM C109-109M [36]. A constant loading rate of 2.5 kN/s was applied to all tested specimens and equivalent compressive strengths were recorded automatically based on the size of the specimens. Once the specimens were broken, they were ground to a fine powder for SEM analysis. Scanning electron microscopy (SEM) with sufficient magnification was used to examine the AAMs' surface morphology.
First, the AAM samples were collected from the specimens tested for compressive strength at 28 days of age, and then each sample was sowed on to double cellophane sheets and then attached to a coin. All specimens were coated in advance using a gold sputter coater machine. Significant morphology images were captured immediately after selecting the sufficient image magnifications.

Mechanical Properties
The impacts of AAM designs with different binder mass constituents on CS are presented in Table 2, Table 3, Table 4, Table 5 and discussed in this section. The 28-day CS of the AAM designs with a high-volume FA substitute is presented in Figure 3. The results indicated that the highest compressive strength was achieved by the GBFS to POFA ratio of 4 with 60% FA. The trend line demonstrates that by increasing the ratio of GBFS to POFA, CS increased for all mix designs with different FA percentages.     Figure 4 shows the 28-day CS versus the ratio of GBFS to FA in AAM designs with a high volume POFA. The results confirmed that by increasing POFA, the CS decreased. Additionally, the trend line shows that increasing the ratio of GBFS to FA improved the CS regardless of POFA percentage. The reduction in CS of this mix design containing POFA is ascribed to the delay in the hydration process as well as the slow pozzolanic activity of POFA, which negatively influences the CS. Figure 5 shows the 28-day CS versus the ratio of FA to POFA in AAM designs with a high volume of GBFS. It is evident that the ratio of FA to POFA had a minor effect on CS. For an almost identical ratio of FA to POFA, the CS increased by around 53% by increasing the GBFS percentage from 50% to 70%.   Figure 5 shows the 28-day CS versus the ratio of FA to POFA in AAM designs with a high volume of GBFS. It is evident that the ratio of FA to POFA had a minor effect on CS. For an almost identical ratio of FA to POFA, the CS increased by around 53% by increasing the GBFS percentage from 50% to 70%.  Figure 6 shows the 28-day CS versus the ratio of GBFS to FA in AAM designs with a high volume of WCP. The results clearly showed that increasing the WCP percentage substantially decreased the CS, where the CS declined from 60 to around 20 MPa by decreasing the WCP from 70% to 50%. Additionally, the results confirmed that CS improves by increasing the ratio of GBFS to FA.  Figure 6 shows the 28-day CS versus the ratio of GBFS to FA in AAM designs with a high volume of WCP. The results clearly showed that increasing the WCP percentage substantially decreased the CS, where the CS declined from 60 to around 20 MPa by decreasing the WCP from 70% to 50%. Additionally, the results confirmed that CS improves by increasing the ratio of GBFS to FA.  Figure 6 shows the 28-day CS versus the ratio of GBFS to FA in AAM designs with a high volume of WCP. The results clearly showed that increasing the WCP percentage substantially decreased the CS, where the CS declined from 60 to around 20 MPa by decreasing the WCP from 70% to 50%. Additionally, the results confirmed that CS improves by increasing the ratio of GBFS to FA.   Figure 7 shows the effects of SiO 2 :Al 2 O 3 and CaO:SiO 2 on 28-days CS of ternary blended AAMs. Depending on the percentages of each industrial waste material in ternary blended AAMs, the following conclusion can be drawn:

Correlate the Strength with the Chemical Composition of the Mixture
i.
In AAMs with high volume FA, the increment in the SiO 2 to Al 2 O 3 ratio resulted in the reaction of Al 2 O 3 content in the earlier stages. Therefore, the gradual increment of the SiO 2 content in further stages provided more silicate for condensation and reaction between the silicate species and this caused the dominance of oligomeric silicates. The domination of SiO 2 content reduced the rate of condensation resulting in gradual hardening of the AAMs (Figure 7a). ii. In AAMs with high volume POFA, the increase in the POFA to GBFS ratio of the AAMs delayed the ultimate CS (Figure 7b). The developed strength was inversely correlated to the silicate to aluminium ratio, which was recorded to be an optimum of 55.6 MPa for a silicate to aluminium ratio of 6.5. iii. In AAMs with high volume GBFS, the 28-days CS was highest (97 MPa) for calcium to silicate ratio of 0.97. A ratio of silicate to aluminium of 2.75 and 3.25 reduced the 28-days CS to 86.4 and 85.1 MPa, respectively (Figure 7c). iv. In AAMs with high volume WCP, it was observed that the compressive strength was enhanced with the decrease in SiO 2 :Al 2 O 3 and the highest 28-days CS (67 MPa) was recorded with calcium to silicate ratio higher than 0.40 (Figure 7d). , respectively (Figure 7c). iv.

MPa
In AAMs with high volume WCP, it was observed that the compressive strength was enhanced with the decrease in SiO2:Al2O3 and the highest 28-days CS (67 MPa) was recorded with calcium to silicate ratio higher than 0.40 (Figure 7d).
Overall, it is evident that an increase in the percentage content of CaO and Al2O3 could enhance the CS of the mortar following the above-mentioned mechanism.  Overall, it is evident that an increase in the percentage content of CaO and Al 2 O 3 could enhance the CS of the mortar following the above-mentioned mechanism. Figure 8 shows the SEM images of the AAM designs with 50% and 70% FA contents after 28 days of curing. The results clearly showed that the specimen with 50% FA possessed less non-reactive particles and micro-cracks compared to 70% FA. Our interpretation of this particular issue is that increasing FA leads to a decrease in CS, as shown in Table 2. It is anticipated that cracks and pores will increase on a larger scale when increasing the FA percentage in AAM designs. The previous literature has also indicated that a reduction in the CS with an increase in FA content was ascribed to the decrease in CaO and increase in SiO 2 content in the mortar's matrix [37,38]. Furthermore, increasing the FA content could generate a low CaO to SiO 2 ratio, leading to the formation of a smaller quantity of C-(A)-S-H gel in the mixtures containing up to 70% FA compared to the mixtures with over 30% addition of FA. It has well known that the increasing content of aluminosilicate materials, such as FA, POFA, and CWP in the alkali-activated matrix led to a rise in the quantity of non-reacted quartz (SiO 2 ) which causes a poor morphology structure and high porosity. The performance of AAMs' strength was adversely influenced by this and showed lower strength values.

Evaluation of SEM Results
increasing the FA content could generate a low CaO to SiO2 ratio, leading to the formation of a smaller quantity of C-(A)-S-H gel in the mixtures containing up to 70% FA compared to the mixtures with over 30% addition of FA. It has well known that the increasing content of aluminosilicate materials, such as FA, POFA, and CWP in the alkali-activated matrix led to a rise in the quantity of non-reacted quartz (SiO2) which causes a poor morphology structure and high porosity. The performance of AAMs' strength was adversely influenced by this and showed lower strength values.  Figure 9 presents the SEM images of the AAM designs for different POFA contents of 50% and 70%. The results confirmed that at a lower POFA content, the specimen was free from cracks. Increasing the POFA content increased the number of unreacted particles and led to a poor binder structure. The results also indicated that in design mixes with a high POFA content, a large amount of silica remained unreacted, leading to a poor alkali-activated binder structure. This issue is also confirmed in Table 3, where the AAM designs with a high content of POFA led to the lowest CS.   Figure 9 presents the SEM images of the AAM designs for different POFA contents of 50% and 70%. The results confirmed that at a lower POFA content, the specimen was free from cracks. Increasing the POFA content increased the number of unreacted particles and led to a poor binder structure. The results also indicated that in design mixes with a high POFA content, a large amount of silica remained unreacted, leading to a poor alkali-activated binder structure. This issue is also confirmed in Table 3, where the AAM designs with a high content of POFA led to the lowest CS.
the decrease in CaO and increase in SiO2 content in the mortar's matrix [37,38]. Furthermore, increasing the FA content could generate a low CaO to SiO2 ratio, leading to the formation of a smaller quantity of C-(A)-S-H gel in the mixtures containing up to 70% FA compared to the mixtures with over 30% addition of FA. It has well known that the increasing content of aluminosilicate materials, such as FA, POFA, and CWP in the alkali-activated matrix led to a rise in the quantity of non-reacted quartz (SiO2) which causes a poor morphology structure and high porosity. The performance of AAMs' strength was adversely influenced by this and showed lower strength values.  Figure 9 presents the SEM images of the AAM designs for different POFA contents of 50% and 70%. The results confirmed that at a lower POFA content, the specimen was free from cracks. Increasing the POFA content increased the number of unreacted particles and led to a poor binder structure. The results also indicated that in design mixes with a high POFA content, a large amount of silica remained unreacted, leading to a poor alkali-activated binder structure. This issue is also confirmed in Table 3, where the AAM designs with a high content of POFA led to the lowest CS.  To gain insight into the waste ceramic powder inclusion with different percentages in the alkali-activated mix designs, the SEM images were investigated, as shown in Figure 10. The result indicated the creation of a larger amount of crystalline Ca(OH) 2 in hexagonal plate-like structures in alkali-activated mix designs with 60% and 70% ceramic contents. This can be explained by the hydration process of an excess amount of CaO in the GBFS and FA, which produces an elevated amount of Ca(OH) 2 crystals. When GBFS is mixed with FA, it shapes a hydrated binding cement paste (HCP) of calcium silicate hydrate (C-S-H). The formation of a massive amount of C-S-H crystals in alkali-activated mix designs with 50% ceramic content made it denser, which is attributed to the pozzolanic reaction of SiO 2 with Ca(OH) 2 during the hydration process. Subsequently, such dense microstructures contribute to enhancing the CS of the mix designs.
process of an excess amount of CaO in the GBFS and FA, which produces an elevated amount of Ca(OH)2 crystals. When GBFS is mixed with FA, it shapes a hydrated binding cement paste (HCP) of calcium silicate hydrate (C-S-H). The formation of a massive amount of C-S-H crystals in alkaliactivated mix designs with 50% ceramic content made it denser, which is attributed to the pozzolanic reaction of SiO2 with Ca(OH)2 during the hydration process. Subsequently, such dense microstructures contribute to enhancing the CS of the mix designs.

Sustainable Properties
The energy consumption for the transformation from a raw material to a refined material is defined as the embodied energy (EE). The EE comprises of energy for collecting (i.e., mining process, grinding process, sieving process) and refining (a group of chemical engineering unit processes and unit operations that refine certain materials or convert raw material into products of value). Energy consumption in these two stages is recognized to be the fundamental source of the embodied energies of building materials. Extra energy is required for machines, transportation, labor and facilities. In this research, a cradle-to-gate EE was used to define the energy required for resource extraction (cradle) to the factory gate (i.e., before it is transported to the consumer). An example of a cradle-togate process for WCP is shown in Figure 11.

Sustainable Properties
The energy consumption for the transformation from a raw material to a refined material is defined as the embodied energy (EE). The EE comprises of energy for collecting (i.e., mining process, grinding process, sieving process) and refining (a group of chemical engineering unit processes and unit operations that refine certain materials or convert raw material into products of value). Energy consumption in these two stages is recognized to be the fundamental source of the embodied energies of building materials. Extra energy is required for machines, transportation, labor and facilities. In this research, a cradle-to-gate EE was used to define the energy required for resource extraction (cradle) to the factory gate (i.e., before it is transported to the consumer). An example of a cradle-to-gate process for WCP is shown in Figure 11. Ca(OH)2 crystals. When GBFS is mixed with FA, it shapes a hydrated binding cement paste (HCP) of calcium silicate hydrate (C-S-H). The formation of a massive amount of C-S-H crystals in alkaliactivated mix designs with 50% ceramic content made it denser, which is attributed to the pozzolanic reaction of SiO2 with Ca(OH)2 during the hydration process. Subsequently, such dense microstructures contribute to enhancing the CS of the mix designs.

Sustainable Properties
The energy consumption for the transformation from a raw material to a refined material is defined as the embodied energy (EE). The EE comprises of energy for collecting (i.e., mining process, grinding process, sieving process) and refining (a group of chemical engineering unit processes and unit operations that refine certain materials or convert raw material into products of value). Energy consumption in these two stages is recognized to be the fundamental source of the embodied energies of building materials. Extra energy is required for machines, transportation, labor and facilities. In this research, a cradle-to-gate EE was used to define the energy required for resource extraction (cradle) to the factory gate (i.e., before it is transported to the consumer). An example of a cradle-togate process for WCP is shown in Figure 11. Figure 11. Cradle-to-gate process to produce ceramic powder from waste ceramics. Figure 11. Cradle-to-gate process to produce ceramic powder from waste ceramics.
The cradle-to-gate EE of each AAM design with different binder mass constituents can be calculated using the following equation.
where EE i and EE AAM are the embodied energies (MJ) of waste materials i and AAM designs i, respectively. m i is the mass of waste material i. It is evident that, upon the application of industrial waste materials, the EE would significantly decrease. Meanwhile, building energy consumption is responsible for approximately 45% of the CO 2 emissions in the atmosphere, which contributes to the greenhouse effect. For instance, emissions of CO 2 from fossil fuel combustion, with contributions from cement manufacture, have been responsible for more than 75% of the increase in atmospheric CO 2 concentrations since pre-industrial times [39]. The cradle-to-gate CO 2 emission of each AAM design with different binder mass constituents can be calculated using the following equation.
where CO 2,i and CO 2, AAM are the CO 2 emission (kg CO 2 /kg) of waste materials i and AAM designs i, respectively. The EE of each employed industrial waste material and the relevant CO 2 emissions are summarized in Table 6. Although the EE of each waste material was calculated by the authors, the accuracy of the estimated values was evaluated by referring to the available guidelines-i.e., the Inventory of Carbon and Energy (ICE) [40]. The results show that OPC required a massive amount of energy for the manufacturing process compared to waste materials, which led to an increase in EE and the release of greenhouse gases.  Table 7 shows the calculated EE and CO 2 emissions for all AAM designs composed of industrial waste materials. Table 7 confirms that the average EE and CO 2 emissions of all studied AAM designs are 1.5 MJ/kg and 0.084 kgCO 2 /kg, which are lower than those of OPC. It is also clear that the AAM designs using high FA contents provided the lowest EE and CO 2 emissions compared to other design mixes.

Developing an Empirical Equation to Predict Compressive Strength
In this section, using a multi linear regression (MLR), an empirical equations are proposed to estimate the CS, EE, and CO 2 emissions based on the proportions of each industrial waste used in the binder mass, as shown in Equations (5) to (7).
These equations were developed based on the proportions of each industrial waste used in the binder mass. Figure 12 shows the scatter graph that provided the relationship between the test and calculated data using an empirical equation for estimating the CS. The average and standard deviation of the proposed empirical equation are 58.5 MPa and 19.6, respectively, compared to 61.3 MPa and 18.7, as calculated by the test results; this indicates the adequacy of the proposed empirical equation. The coefficient of determination (R 2 ), which determines the overall change in the dependent variables calculated by the linear regression equation, Equation (5), was 0.8715, which is relatively acceptable, providing good confidence in the relationship. calculated data using an empirical equation for estimating the . The average and standard deviation of the proposed empirical equation are 58.5 MPa and 19.6, respectively, compared to 61.3 MPa and 18.7, as calculated by the test results; this indicates the adequacy of the proposed empirical equation. The coefficient of determination (R 2 ), which determines the overall change in the dependent variables calculated by the linear regression equation, Equation (5), was 0.8715, which is relatively acceptable, providing good confidence in the relationship.  Figure 13 shows the comparison between observational (test) and computational (MLR) methods of all 42 specimens for estimating the CS. It is clear that except for some specimens, the MLR approach properly estimated the CS.  Figure 13 shows the comparison between observational (test) and computational (MLR) methods of all 42 specimens for estimating the CS. It is clear that except for some specimens, the MLR approach properly estimated the CS.  Figures 14 and 15 show the scatter graph that provided the relationship between the test and calculated data, estimated by an empirical Equations (6) and (7), for estimating the EE and CO2 emission, respectively. The coefficient of determination (R 2 ) is estimated as 0.98 for both EE and CO2 emissions, indicating the adequacy of the proposed equations.   Figures 14 and 15 show the scatter graph that provided the relationship between the test and calculated data, estimated by an empirical Equations (6) and (7), for estimating the EE and CO 2 emission, respectively. The coefficient of determination (R 2 ) is estimated as 0.98 for both EE and CO 2 emissions, indicating the adequacy of the proposed equations.  Figures 14 and 15 show the scatter graph that provided the relationship between the test and calculated data, estimated by an empirical Equations (6) and (7), for estimating the EE and CO2 emission, respectively. The coefficient of determination (R 2 ) is estimated as 0.98 for both EE and CO2 emissions, indicating the adequacy of the proposed equations.

Conclusions
In this study, the 28-day CS of zero OPC mortar with ternary blended AAM designs composed of industrial waste materials (FA, GBFS, POFA, and WCP) were investigated. The results confirmed that the CS of these environmentally friendly AAM designs were satisfactory, with an average of 61.3 MPa. According to the test results from different ternary blended AAM designs and relevant contents of constituents, the following conclusions were reached: 1. The X-ray fluorescence spectroscopy (XRF) results confirmed that the ratio of GBFS to FA significantly controls the SiO2, CaO, and Al2O3 contents in ternary blended AAM designs.
2. AAM designs with a high volume of GBFS provided the highest 28-day CS, were in these ternary blended mixes. The ratio of FA to POFA had a minor effect on CS; however, increasing the GBFS percentage substantially improved the CS.
3. The CS in all AAM designs declined as a result of increasing the FA content. SEM images also confirmed that the AAM designs using 50% FA possessed less non-reactive particles and microcracks compared with 70% FA. 4. The CS in AAM designs with a high volume of WCP and FA was ranked the lowest among all AAM designs-at around 20 MPa. SEM images also confirmed that the formation of a large amount of C-S-H crystals in AAM designs with a low content of WCP increased the density, which was attributed

Conclusions
In this study, the 28-day CS of zero OPC mortar with ternary blended AAM designs composed of industrial waste materials (FA, GBFS, POFA, and WCP) were investigated. The results confirmed that the CS of these environmentally friendly AAM designs were satisfactory, with an average of 61.3 MPa. According to the test results from different ternary blended AAM designs and relevant contents of constituents, the following conclusions were reached: 1.
The X-ray fluorescence spectroscopy (XRF) results confirmed that the ratio of GBFS to FA significantly controls the SiO 2 , CaO, and Al 2 O 3 contents in ternary blended AAM designs.

2.
AAM designs with a high volume of GBFS provided the highest 28-day CS, were in these ternary blended mixes. The ratio of FA to POFA had a minor effect on CS; however, increasing the GBFS percentage substantially improved the CS.

3.
The CS in all AAM designs declined as a result of increasing the FA content. SEM images also confirmed that the AAM designs using 50% FA possessed less non-reactive particles and micro-cracks compared with 70% FA. 4.
The CS in AAM designs with a high volume of WCP and FA was ranked the lowest among all AAM designs-at around 20 MPa. SEM images also confirmed that the formation of a large amount of C-S-H crystals in AAM designs with a low content of WCP increased the density, which was attributed to the pozzolanic reaction of SiO 2 with Ca(OH) 2 during the hydration process. 5.
The industrial waste materials had significantly lower EE and CO 2 emissions compared to OPC. The AAM designs that contained a high FA content provided the lowest EE and CO 2 emissions compared to other design mixes.