Reuse of Eggshell Waste and Recycled Glass in the Fabrication Porous Glass–Ceramics

: This study was conducted to fabricate and characterize of glass–ceramic foam derived from soda-lime silica (SLS) glass waste and eggshell (ES) waste as a foaming agent by using empirical formula [ES] × [SLS] 100 − x where x = 1 wt %, 3 wt %, 6 wt %, 9 wt %. The samples undergo a heat-treatment process at temperature 800 ◦ C with a heating rate of 10 ◦ C / min. The properties of the samples were measured by average density measurement and linear expansion. The structural properties were studied by XRD, FESEM and FTIR concerning the di ﬀ erent composition of the foaming agent while the mechanical properties were determined by compressive strength using UTM. The lowest density and compressive strength were achieved by 0.326 g / cm 3 and 0.04 MPa, respectively with the highest linear expansion at 77.33% by the addition of 3 wt % of ES. Moreover, the cristobalite phase (SiO 2 ) were identiﬁed after the heat treatment process. The production of foam glass–ceramics using SLS glass and ES can be applied to prepare di ﬀ erent type of porosity that gives beneﬁt to the environment and energy usage.


Introduction
Globally, the increase of organic and inorganic waste caused by increasing human population growth as well as their lifestyle. Discarded waste such as waste glasses give a negative impact on the environment. For instance, the discarded cathode ray tube (CRT) panel from the electronic component and soda-lime-silica glass from the automotive industry are polluted with heavy metals [1,2]. To overcome this problem, both raw materials are utilized for making valuable materials such as manufacturing stoneware tiles, production of concrete blocks, fabrication of glass-ceramics materials, and the manufacture of foam glass-ceramics [3]. There is a wide sector application used to insulate the materials such as the construction industry, biochemistry industry, material engineering, military security, etc. [4].
Foam glass-ceramic is a thermal insulation material that has attracted much attention nowadays, function to retard heat flow due to its properties such as high thermal resistance. Generally, the foam glass is a solid bulk material, shaped by mixing the glass powder and foaming agent and then undergo a sintering process to form a porous structure. After the softening point temperature of the glass is reached, the solid phase turns to viscous liquid and facilitates the bubbles to grow inside the glass melt, hence foam formation has occurred when solidified the glass melt. The glass can provide an amorphous phase that led to better thermal insulation material s appearance. The pores were generated The raw material used in this research were SLS glass waste bottle, ES as a foaming agent and polyvinyl alcohol (PVA) as a binder. The SLS glass waste was collected from the glass bottle of sauce (Brand: Life) from Pizza Hut IOI City Mall Putrajaya, Malaysia. The waste glass is usually contaminated from dirt and it must be washed before crushing. ES was collected from recycling containers located at Sri Serdang, Selangor, Malaysia restaurants which then rinsed with water and dried for 24 h in the dry oven before crushing. This process used to completely remove all dirt on the ES. Waste SLS glass and ES were crushed into the small glass cullet. The glass cullet then placed into milling jar with ceramic balls and was left at milling machine (US Stoneware Corp) for 24 h at the speed of 50 rpm to get a fine glass powder. Then, the glass powder was filtered to obtain the powder with 45 µm particle size using stainless steel sieve while the ES ground using pestle and mortar and sieve into 45 µm size. Figure 1 shows the flowchart of the sample preparation. First, SLS glass and ES powder were prepared with different weight percentages and weighed using a digital analytical balance. Both powders were put in a bottle according to the empirical formula and mix by using pestle and mortar. Then, the homogenous powder was pressed using a (Specac, Ltd., Orpington, UK) hydraulic pressing machine, with an applied load of 5 MPa for 10-15 min and transformed into pellet form, 13.10-mm diameter. The pellets placed into the alumina boat and went for the heat-treatment process. All samples were heat-treated at 800 • C for 1 h by using the electric furnace. After the heat treatment process, the pellets were grounded into 45 µm in size and were sent to characterization.
Appl. Sci. 2020, 10, x FOR PEER REVIEW 3 of 12 samples were heat-treated at 800 °C for 1 h by using the electric furnace. After the heat treatment process, the pellets were grounded into 45 μm in size and were sent to characterization. Wavelength dispersive X-ray fluorescence (WD-XRF), (Bruker, S8 Tiger, Billerica, MA, USA) was used to analyze SLS and ES powder to identify chemical composition in both raw materials. Thermogravimetric Analyzer-Mettler Toledo (TGA/SDTA 851, Columbus, OH, USA) was used to determine the weight loss decomposition of ES with the temperature in the range of 27-1000 °C. The finding results as shown in Table 1 and Figure 1 for XRF and TGA analysis, respectively. The bulk density (ρ) of the produced foam was measured by the Archimedes principle and the formula as shown in Equation (1).

= =
(1) Wavelength dispersive X-ray fluorescence (WD-XRF), (Bruker, S8 Tiger, Billerica, MA, USA) was used to analyze SLS and ES powder to identify chemical composition in both raw materials. Thermogravimetric Analyzer-Mettler Toledo (TGA/SDTA 851, Columbus, OH, USA) was used to determine the weight loss decomposition of ES with the temperature in the range of 27-1000 • C. The finding results as shown in Table 1 and Figure 1 for XRF and TGA analysis, respectively. The bulk density (ρ) of the produced foam was measured by the Archimedes principle and the formula as shown in Equation (1).
where W air is a weighted sample in air, W water is a weighted sample in water and p is a density of water.
Appl. Sci. 2020, 10, 5404 4 of 12 The porosity was evaluated by comparing Archimedes analysis to true density using Brunauer-Emmett-Teller (BET) surface analysis. The ratio between density as follows: where p b is a bulk density, p t is a true density. The linear expansion (LE) of the produced material was measured by subtracting the diameter of the glass-ceramic pellet (D f ) after it was treated to the diameter of the glass-ceramic before treated (D i ) using digital vernier caliper (Mitutoyo 500-196-20, Kanagawa, Japan). The percentage linear expansion of the treated foam glass-ceramic sample was determined using Equation (3).
X-ray diffraction (XRD) was made from MPD X'PERT PRO PANalytical's (Philips, PW 3040/60, Almelo, The Netherlands and Malvern, UK) with Cu-Kα radiation in the 20 range from 20 • to 80 • . The software X Pert Highscore plus software (PANalytical) was used to identify the crystal phase of foam glass-ceramics. The crystal phase content or crystallinity (%) was evaluated by Origin 8 software based on a semicrystalline pattern of XRD. The formula of the crystal phase is where C is the crystallinity or crystal content (%), A C is the diffraction peak area of the crystalline phase and A A is the scattering peak area of the amorphous phase. The diffraction peak area of the crystalline phase was determined by the calculation of full width at half maximum (FHWM). The sample undergoes FTIR analysis to identify the functional group of the sample from spectra recorded using FTIR Nicolet 6700 (Thermo Nicolet, Waltham, MA, USA) with 400-4000 nm of wavenumber. The morphology and microstructure of the foam glass-ceramics were analyzed by using FESEM Nova NanoSEM 230 (FEI, Hillsboro, OR, USA) and the size of pores diameter was evaluated by ImageJ software. The compressive strength was measured by using Universal Testing Machine (Instron 5566, Norwood, MA, USA) with a 10 kN load of compression and crosshead speed at 0.5 mm/min. Before testing the strength, the inhomogeneous surface of foam glass-ceramics was refined by using a hacksaw and SiC abrasive paper then all the samples were cut to get a standardized size of~14.0 mm × 8.0 mm of the disc. The compressive strength was determined by stress-strain curve analysis and recorded the average for each sample (n = 5).

Composition of SLS Glass and ES
Each of the precursor SLS glass and ES were chemically analyzed by using Wavelength Dispersive X-ray Fluorescence (WDXRF). The elemental analysis was measured in the oxide form as tabulated in Table 1. The chemical composition of the SLS glass waste in this research was similar to the SLS glass bottles. The ES used as a foaming agent mainly contained calcium carbonate (CaCO 3 ). From Table 1, there was 95 wt % account for the element of SiO 2 , CaO and Na 2 O remarked the main constituents of the precursor glass. Meanwhile, the remaining percentage of other oxide elements were Al 2 O 3 and MgO from the total composition of the precursor glasses.
ES powder undergoes TGA analysis to determine the weight loss decomposition of calcium carbonate, CaCO 3 to carbon dioxide, CO 2, and calcium oxide, CaO in the ratio 1:1. Figure 2 illustrates the TGA analysis of ES showed that the loss mass of calcium carbonate. The calcium carbonate starts to decompose about 6% of mass at 680 • C of temperature at the first stage and the second stage, the mass loss of calcium carbonate was intensified by 41% to carbon dioxide, CO 2 and the other 53% was calcium oxide, CaO at 810 • C of temperature. The finding percentage mass loss of calcium oxide was agreed with XRF analysis as shown in Table 1. After 810 • C of temperature, there was no more decompose of calcium carbonate. The weight loss of carbonate relative to the temperature in this research is similar to the previous study which states that decompose temperature of eggshell in the range of 700-850 • C of temperature [14]. Therefore, 800 • C of temperature was selected as the sintering temperature in this research.
Appl. Sci. 2020, 10, x FOR PEER REVIEW 5 of 12 the TGA analysis of ES showed that the loss mass of calcium carbonate. The calcium carbonate starts to decompose about 6% of mass at 680 °C of temperature at the first stage and the second stage, the mass loss of calcium carbonate was intensified by 41% to carbon dioxide, CO2 and the other 53% was calcium oxide, CaO at 810 °C of temperature. The finding percentage mass loss of calcium oxide was agreed with XRF analysis as shown in Table 1. After 810 °C of temperature, there was no more decompose of calcium carbonate. The weight loss of carbonate relative to the temperature in this research is similar to the previous study which states that decompose temperature of eggshell in the range of 700-850 °C of temperature [14]. Therefore, 800 °C of temperature was selected as the sintering temperature in this research.

Physical and Mechanical Analysis
Bulk density of the foam glass-ceramics for 1, 3, 6 wt% and 9 wt% ES were 1.215, 0.326, 0.421 and 0.822 g/cm 3, respectively. The trend for the bulk density was similar to the compressive strength value. Figure 3 indicates the trend of bulk density-porosity of foam glass-ceramics at different content of ES. Porosity is calculated with the constant value of ρpowder = 2.5 g/cm 3 . The porosity was indirectly proportional to the bulk density. Figure 2 shows the minimum density was achieved from 3 wt% ES with 87% of porosity. Meanwhile, the maximum density was 1.215 g/cm 3 from 1 wt% ES with the lowest porosity of 51.4%. The value is in the range of commercial foam glass, which is 0.1-1.2 g/cm 3 [15]. Linear expansion of a sample is the changing of size and dimension of the sample thus higher of linear expansion percentage contributes to the reducing volume of the sample. The linear expansion curve as shown in Figure 4, shows that the linear expansion value have an insignificant difference between 1 wt% and 9 wt% ES. The maximum linear expansion from 3 wt% ES with the value was 77.33% meanwhile the minimum linear expansion was 59.62% from 9 wt% ES. Therefore, decreasing in a volume of foam glass-ceramics would give to the high density. The difference value of density caused by the difference content of ES. The higher content of ES would have an increasing amount of crystallite hence give increasing the viscosity of the system [14].

Physical and Mechanical Analysis
Bulk density of the foam glass-ceramics for 1, 3, 6 wt % and 9 wt % ES were 1.215, 0.326, 0.421 and 0.822 g/cm 3, respectively. The trend for the bulk density was similar to the compressive strength value. Figure 3 indicates the trend of bulk density-porosity of foam glass-ceramics at different content of ES. Porosity is calculated with the constant value of ρ powder = 2.5 g/cm 3 . The porosity was indirectly proportional to the bulk density. Figure 2 shows the minimum density was achieved from 3 wt % ES with 87% of porosity. Meanwhile, the maximum density was 1.215 g/cm 3 from 1 wt % ES with the lowest porosity of 51.4%. The value is in the range of commercial foam glass, which is 0.1-1.2 g/cm 3 [15]. Linear expansion of a sample is the changing of size and dimension of the sample thus higher of linear expansion percentage contributes to the reducing volume of the sample. The linear expansion curve as shown in Figure 4, shows that the linear expansion value have an insignificant difference between 1 wt % and 9 wt % ES. The maximum linear expansion from 3 wt % ES with the value was 77.33% meanwhile the minimum linear expansion was 59.62% from 9 wt % ES. Therefore, decreasing in a volume of foam glass-ceramics would give to the high density. The difference value of density caused by the difference content of ES. The higher content of ES would have an increasing amount of crystallite hence give increasing the viscosity of the system [14].  The compressive strength of foam glass-ceramics was determined by stress-strain curve analysis as shown in Figure 5. From the stress-strain curve, the ultimate strength point was determined beyond before the cracking of the samples [16,17]. The curve for 3 wt% of ES was slightly invisible because of the minimum value of the strength of 0.04 MPa. The maximum compressive strength from 9 wt% ES which was 0.81 MPa. Figure 6 shows the relation of porosity-compressive strength respective to the different content of the foaming agent. From the graph, the compressive strength was decreased drastically from 1 wt% to 3 wt% ES and increase slightly as adding more ES content to the 6 wt% and 9 wt%. The lowest strength from 3 wt% ES which was 0.04 MPa with the highest porosity. This is indicating that low in strength caused by high in porosity attributed to the expansion of the samples. Meanwhile, there was a significant difference in compressive strength between 1 wt% and 3 wt% ES. There may be an insufficient amount of CO2 gas generated in from 1 wt% ES. In fact, the high content of SiO2 can cause a lack of liquid phase thus no expansion [18].  The compressive strength of foam glass-ceramics was determined by stress-strain curve analysis as shown in Figure 5. From the stress-strain curve, the ultimate strength point was determined beyond before the cracking of the samples [16,17]. The curve for 3 wt% of ES was slightly invisible because of the minimum value of the strength of 0.04 MPa. The maximum compressive strength from 9 wt% ES which was 0.81 MPa. Figure 6 shows the relation of porosity-compressive strength respective to the different content of the foaming agent. From the graph, the compressive strength was decreased drastically from 1 wt% to 3 wt% ES and increase slightly as adding more ES content to the 6 wt% and 9 wt%. The lowest strength from 3 wt% ES which was 0.04 MPa with the highest porosity. This is indicating that low in strength caused by high in porosity attributed to the expansion of the samples. Meanwhile, there was a significant difference in compressive strength between 1 wt% and 3 wt% ES. There may be an insufficient amount of CO2 gas generated in from 1 wt% ES. In fact, the high content of SiO2 can cause a lack of liquid phase thus no expansion [18].  The compressive strength of foam glass-ceramics was determined by stress-strain curve analysis as shown in Figure 5. From the stress-strain curve, the ultimate strength point was determined beyond before the cracking of the samples [16,17]. The curve for 3 wt % of ES was slightly invisible because of the minimum value of the strength of 0.04 MPa. The maximum compressive strength from 9 wt % ES which was 0.81 MPa. Figure 6 shows the relation of porosity-compressive strength respective to the different content of the foaming agent. From the graph, the compressive strength was decreased drastically from 1 wt % to 3 wt % ES and increase slightly as adding more ES content to the 6 wt % and 9 wt %. The lowest strength from 3 wt % ES which was 0.04 MPa with the highest porosity. This is indicating that low in strength caused by high in porosity attributed to the expansion of the samples. Meanwhile, there was a significant difference in compressive strength between 1 wt % and 3 wt % ES. There may be an insufficient amount of CO 2 gas generated in from 1 wt % ES. In fact, the high content of SiO 2 can cause a lack of liquid phase thus no expansion [18].

Structural Analysis
As discussed on the physical properties of foam glass-ceramics earlier, the finding can be verified through microstructure analysis as shown in Figure 7. Figure 7 shows that the pore distribution closed pores of foam glass-ceramics at different content of ES. Based on Figure 7a, it shows that the small pores appeared with homogeneously distributed. The average size of the pore diameter was 682 μm. Increasing the ES content to the 3 wt% gives a significant difference in the pore size as shown in Figure 7b. Therefore, the diameter of the pore distributed from 3 wt% ES was in the range of 870-1500 μm. The pores revealed from 6 wt% ES as shown in Figure 7c

Structural Analysis
As discussed on the physical properties of foam glass-ceramics earlier, the finding can be verified through microstructure analysis as shown in Figure 7. Figure 7 shows that the pore distribution closed pores of foam glass-ceramics at different content of ES. Based on Figure 7a, it shows that the small pores appeared with homogeneously distributed. The average size of the pore diameter was 682 μm. Increasing the ES content to the 3 wt% gives a significant difference in the pore size as shown in Figure 7b. Therefore, the diameter of the pore distributed from 3 wt% ES was in the range of 870-1500 μm. The pores revealed from 6 wt% ES as shown in Figure 7c

Structural Analysis
As discussed on the physical properties of foam glass-ceramics earlier, the finding can be verified through microstructure analysis as shown in Figure 7. Figure 7 shows that the pore distribution closed pores of foam glass-ceramics at different content of ES. Based on Figure 7a, it shows that the small pores appeared with homogeneously distributed. The average size of the pore diameter was 682 µm. Increasing the ES content to the 3 wt % gives a significant difference in the pore size as shown in Figure 7b. Therefore, the diameter of the pore distributed from 3 wt % ES was in the range of 870-1500 µm. The pores revealed from 6 wt % ES as shown in Figure 7c was insignificant different from pore distribution between 3 wt % ES. However, the microstructure shows that there was an inhomogeneous pore distribution; indicate small pores which the size of diameter in the range of 250-350 µm while for large pores in the range of 861-1200 µm of diameter. This phenomenon occurs due to the high internal pressure inside the pores. Indeed, the high content of the foaming agent would increase the gas pressure and outweighs the strength of pore walls, thus making open pores in the surface [19]. Moreover, the previous research by using banana leaves as a foaming agent stated that the samples contain high banana leaves could cause the release of gases as a result break of the pore's wall and coalescence of pores occur [20]. Meanwhile, as an increasing amount of ES to 9 wt %, it can see the decrease in pores, 508-700 µm of diameter as shown in Figure 7d due to the high viscosity of the system. The changing of viscosity influenced by the crystallization process inside the glass melt [21]. The previous research study by using coal fly ash and CaCO 3 revealed that pores are homogenized sized obtained with 6% of calcium carbonate [22].
Appl. Sci. 2020, 10, x FOR PEER REVIEW 8 of 12 different from pore distribution between 3 wt% ES. However, the microstructure shows that there was an inhomogeneous pore distribution; indicate small pores which the size of diameter in the range of 250-350 μm while for large pores in the range of 861-1200 μm of diameter. This phenomenon occurs due to the high internal pressure inside the pores. Indeed, the high content of the foaming agent would increase the gas pressure and outweighs the strength of pore walls, thus making open pores in the surface [19]. Moreover, the previous research by using banana leaves as a foaming agent stated that the samples contain high banana leaves could cause the release of gases as a result break of the pore's wall and coalescence of pores occur [20]. Meanwhile, as an increasing amount of ES to 9 wt%, it can see the decrease in pores, 508-700 μm of diameter as shown in Figure 7d due to the high viscosity of the system. The changing of viscosity influenced by the crystallization process inside the glass melt [21]. The previous research study by using coal fly ash and CaCO3 revealed that pores are homogenized sized obtained with 6% of calcium carbonate [22].  Figure 8 shows the XRD pattern of 1 wt%, 3 wt%, 6 wt% and 9 wt% ES at 800 °C of temperature. There was a sharp peak of cristobalite (SiO2, 96-900-8228) at 1 wt% ES because of the high content of SiO2 while a little growth of wollastonite (CaSiO3, 96-900-5778) with 33.26% of crystallinity. Percent of the crystallinity of the semicrystalline phase was determined and evaluated. The amorphous region exists as a broad hump in the range of 21-35° of 2θ meanwhile the crystalline phase was formed underlying the amorphous phase. The observed peak of the crystalline phase was compared with the reference pattern by the Crystallography Open Database (COD). Therefore, the finding peak in this research was cristobalite (SiO2, 96-900-8228) located at ~22° of 2θ and wollastonite (CaSiO3, 96-  Figure 8 shows the XRD pattern of 1 wt %, 3 wt %, 6 wt % and 9 wt % ES at 800 • C of temperature. There was a sharp peak of cristobalite (SiO 2 , 96-900-8228) at 1 wt % ES because of the high content of SiO 2 while a little growth of wollastonite (CaSiO 3 , 96-900-5778) with 33.26% of crystallinity. Percent of the crystallinity of the semicrystalline phase was determined and evaluated. The amorphous region exists as a broad hump in the range of 21-35 • of 2θ meanwhile the crystalline phase was formed underlying the amorphous phase. The observed peak of the crystalline phase was compared with the reference pattern by the Crystallography Open Database (COD). Therefore, the finding peak in this research was cristobalite (SiO 2 , 96-900-8228) located at~22 • of 2θ and wollastonite (CaSiO 3 , 96-900-5778) located 27 • , 29 • , 30 • and 32 • of 2θ. As increasing ES content to 3 wt %, 6 wt % and 9 wt %, the crystallinity was 37.89%, 38.19% and 66.80%, respectively. The high crystal content from 9 wt %, which contributes to the high viscosity of glass melt. Consequently, it would give an     Homogeneous silica is formed only by Si-O-Si bonds meanwhile heterogeneous silica atom is formed with different bonds other than silica. An asymmetric stretch network of silica is increased with the presence of heteroatom meanwhile symmetric of silica bonding is decreased. The band of Ca-O was slight intense for 6 wt % and 9 wt % ES at 600 cm −1 of wavenumber compared to the 1 wt % and 3 wt % ES due to the growth of CaSiO 3 as found in XRD analysis meanwhile, the band of symmetric, vs. SiO 2 at~750 cm −1 of wavenumber were decreased due to the bonding of heteroatom, Ca-Si-O. The wavenumber of asymmetric, v a of Si-O was located in the range of 800-1250 cm −1 indicate the main strong peak with the rich in phase because of the presence of silica in SLS glass powder. Moreover, the wider band at 950 cm −1 of wavenumber was caused by the superposition of the absorption peak related to the stretching vibration of bridging and nonbridging Si-O chemical bonds [24]. Consequently, it promotes the migration of the ions, Ca, and change the structural silica network. The band at 1440-1450 cm −1 of wavenumber assigned that band of carbonate, C-O group. As increasing the content of ES to 9 wt % of ES the band indicates strongly intense at 1450 cm −1 of wavenumber compared to the band at 1 wt %-6 wt % of ES. This is because of the partial decomposition of calcium carbonate from ES to carbon dioxide at 810 • C of temperature as discussed from TGA analysis. There is a little amount of calcium carbonate at high content of ES since the other previous study stated that calcium carbonate is undetectable above 824 • C of temperature [25]. Lastly, there was a slight peak located in the range of 2050-2250 cm −1 represent the ambient of carbon dioxide, CO 2 the main element in this research [26].
strong peak with the rich in phase because of the presence of silica in SLS glass powder. Moreover, the wider band at 950 cm −1 of wavenumber was caused by the superposition of the absorption peak related to the stretching vibration of bridging and nonbridging Si-O chemical bonds [24]. Consequently, it promotes the migration of the ions, Ca, and change the structural silica network. The band at 1440-1450 cm −1 of wavenumber assigned that band of carbonate, C-O group. As increasing the content of ES to 9 wt% of ES the band indicates strongly intense at 1450 cm −1 of wavenumber compared to the band at 1 wt%-6 wt% of ES. This is because of the partial decomposition of calcium carbonate from ES to carbon dioxide at 810 °C of temperature as discussed from TGA analysis. There is a little amount of calcium carbonate at high content of ES since the other previous study stated that calcium carbonate is undetectable above 824 °C of temperature [25]. Lastly, there was a slight peak located in the range of 2050-2250 cm −1 represent the ambient of carbon dioxide, CO2 the main element in this research [26].

Conclusions
In present work, foam glass-ceramics with low in bulk density and relatively high compressive strength can be produced from a mixture of waste SLS glass and ES as a foaming agent by heat treatment process at 800 °C of temperature for 60 min. The content of ES gives an effect on bulk density, porosity, linear expansion and compressive strength. Foam glass-ceramics that have low in bulk density (0.421 g/cm 3 ) and high compressive strength (0.22 MPa) from 6 wt% ES. In terms of structural properties, the increase in the content of ES led to the smaller number of pores caused by high densification of the glass matrix. Moreover, the highest crystal phase content such as wollastonite would hinder the foam formation and give an impact to the properties of foam glassceramics that influenced by the crystallization process in the glass melt. In a nutshell, the preparation of foam glass-ceramic as the porous structure derived from waste materials would give benefit to the economy and environment issue. It is a useful material to the various application in the industry depending on the type of porous structure.

Conclusions
In present work, foam glass-ceramics with low in bulk density and relatively high compressive strength can be produced from a mixture of waste SLS glass and ES as a foaming agent by heat treatment process at 800 • C of temperature for 60 min. The content of ES gives an effect on bulk density, porosity, linear expansion and compressive strength. Foam glass-ceramics that have low in bulk density (0.421 g/cm 3 ) and high compressive strength (0.22 MPa) from 6 wt % ES. In terms of structural properties, the increase in the content of ES led to the smaller number of pores caused by high densification of the glass matrix. Moreover, the highest crystal phase content such as wollastonite would hinder the foam formation and give an impact to the properties of foam glass-ceramics that influenced by the crystallization process in the glass melt. In a nutshell, the preparation of foam glass-ceramic as the porous structure derived from waste materials would give benefit to the economy and environment issue. It is a useful material to the various application in the industry depending on the type of porous structure.