Low-Carbon Composite Based on MOC, Silica Sand and Ground Porcelain Insulator Waste

Abstract

Magnesium oxychloride cement-based composites (MOC) with silica sand/porcelain waste blended fillers were designed and tested. The objective of the presented research was to design and test low carbon, eco-friendly and viable alternatives to Portland cement-based materials. To make new materials environmentally acceptable and sustainable, silica sand applied in the reference composite material was partially substituted by ground porcelain waste (PW) coming from used electrical insulators. The sand substitution ratio was 5, 10, and 15 vol.%. The chemical and mineralogical composition, morphology, and particle size distribution of porcelain waste were measured. For silica sand, porcelain waste, and MgO, specific density, loose bulk density, and Blaine fineness were determined. The effect of porcelain waste on the workability of fresh composite mixtures was characterized by spread diameter. The composites were characterized by their basic structural, mechanical, hygric, and thermal properties. The phase composition and thermal stability at high temperatures of MOC/porcelain waste pastes were also analyzed. Fourier-transform infrared spectroscopy (FT-IR) analysis helped to indicate main compounds formed within the precipitation of MOC phases and their reaction with porcelain waste. The usage of porcelain waste greatly decreased the porosity of composite matrix, which resulted in high mechanical resistance and reduced and decelerated water imbibition. The 10% sand substitution with porcelain waste brought the best mechanical resistance and the lowest water absorption due to the formation of amorphous phases, water-insoluble aluminosilicates. In case of the thermal performance of the examined composites, the low thermal conductivity of porcelain waste was the contradictory parameter to porosity and the high thermal stability of the phases present in porcelain slightly decreased the thermal decomposition of composites with porcelain waste dosage. Based on the results emerged from the experimental tests it was concluded that the partial substitution of silica sand in MOC composites enabled the development of materials possessing interesting and advanced function and technical parameters.

1. Introduction

In the building industry, the tendency towards eco-friendly materials gradually grows due to the increasing rate of pollution. This trend is manifested in the continuous search for alternative materials to the widespread Portland cement (PC), mostly because of the enormous amount of released carbon dioxide connected with its production. The manufacturing process of production of PC is assigned with approximately 7% of the total anthropogenic emissions of CO₂ [1]. The energy consumption of this procedure is also very large, mostly due to the high temperature of clinkering (approx. 15% of industrial energy consumption) [2]. One of the possible alternatives is magnesium oxychloride cement.

Magnesium oxychloride cement (MOC) is an alternative non-hydraulic binder obtained by mixing MgO powder with aqueous solution of MgCl₂. This has been known since 1867, when it was invented by French engineer Stanislas Sorel [3]. The term magnesium oxychloride cement includes various compounds in the system MgO-MgCl₂-H₂O. The four commonly known phases are Phase 3, Phase 5, Phase 2 and Phase 9. Phase 3 (3Mg(OH)₂∙MgCl₂∙8H₂O) and Phase 5 (5Mg(OH)₂∙MgCl₂∙8H₂O) can be prepared at ambient temperature and are the two main phases responsible for the hardness of MOC. They react with the CO₂ from the atmosphere while forming magnesium carbonates [4,5,6,7]. The ability to capture CO₂ during carbonation in combination with the lower calcining temperature of the raw materials makes it superior to PC in terms of the emissions of CO₂ and the negative influence on the environment. Tang et al. reported that the total carbon foot print of MOC-based materials linked with their whole life cycles is by 40–50% lower than that of PC [8]. The other two phases, Phase 2 (2Mg(OH)₂∙MgCl₂∙4H₂O) and Phase 9 (9Mg(OH)₂∙MgCl₂∙5H₂O) can be prepared and are stable at elevated temperatures (~100 °C) [9,10]. MOC has very specific properties, which make it in some ways superior to PC. The distinctly lower specific density of MOC gives it higher compressive and flexural strength. It has high fire resistance, as well as the resistance to abrasion and low thermal conductivity [11,12]. The curing time of MOC is quite short—phase 5 cures fully after approximately 96 h, phase 3 only in 36 h [13,14]. Primarily, MOC is used as a material for flooring, fire protective systems, grinding wheels, wall insulation and as a material for decorative elements [15,16,17,18,19,20]. Also, it is suitable for use with many aggregates, e.g., tire rubber, synthetic resin, wood particles or fly ash [21,22,23,24].

Another direction of the search for alternative materials is linked to the use of natural sources, which needs to be minimized. In the Portland cement concrete production, the consumption of sand is large, while the raw material is quite uncommon. It is possible to replace the sand with alternative waste materials, such as porcelain electric insulation waste. Porcelain electric insulators have very good mechanical strength. The main phases present in their structure are corundum, cristobalite, mullite, quartz and a glass phase fraction [25]. Porcelain insulators are removed after quite a long time of service as a mechanical support for the conductor and its electrical insulation from the grounded structure. They are mechanically stressed by the weight of the conductor and also, they are exposed to weather fluctuation, which might cause some deterioration of the mechanical properties. However, mostly the insulators are capable of serving elsewhere [26,27]. The replacement of ordinarily used sand with porcelain electric insulator waste in concrete was already studied in the past, showing its ability to partially replace the silica sand [28,29]. Moreover, porcelain waste can be considered as CO₂ zero material, when neglecting the energy consumed for its milling.

The objective of this study was the preparation and evaluation of the composite of MOC with porcelain waste sand as a partial replacement for natural sand. The obtained samples were studied using a broad spectrum of analytical methods, to determine their chemical and phase composition, thermal behavior and mechanical properties.

2. Experimental

2.1. Materials and Samples

MOC composites were produced from caustic MgO powder, MgCl₂∙6H₂O of p.a. purity, silica sand, and ground porcelain insulator waste. MgO powder was a product of Styromagnesit Steirische Magnesitindustrie Ltd., Oberdorf, Austria. MgCl₂∙6H₂O was obtained from the Czech chemical company Lach-Ner, Ltd., Brno Neratovice, Czech Republic. As reference aggregate, standardized sand originally produced for rendering and plastering mortars was used. It was delivered by Filtrační písky Ltd. (Chlum u Doks, Czech Republic) and contained three sand fractions with the particles in the 0–2 mm range. The particular sand fractions were mixed in a weight ratio 1:1:1. For the partial substitution of silica sand, porcelain waste (PW) coming from the replacement of used electrical insulators was used in the composition of the developed composites. The porcelain insulators were originally produced by the company Elektroporcelán a.s. (Louny, Czech Republic). At first, they were roughly crushed and then dry milled using a ball mill type Los Angeles.

The composite mixtures were proportioned as introduced in

Table 1. Composition of magnesium oxychloride cement (MOC) composites (g).

Material	MgO	MgCl2	Water	Silica Sand	Porcelain Waste
MOC-Ref	1541.25	682.85	567.25	3 × 1125.00	-
MOC-SPW5	1541.25	682.85	567.25	3 × 1068.75	141.67
MOC-SPW10	1541.25	682.85	567.25	3 × 1012.50	283.33
MOC-SPW15	1541.25	682.85	567.25	3 × 956.25	425.00

. The reference composite was labelled as MOC-Ref. In accordance with sand substitution ratio, materials with incorporated porcelain waste were marked as MOC-SPW5, MOC-SPW10, and MOC-SPW15, respectively. The MOC composites was prepared as prescribed in the EN 14016-2 [30].

The plastic molds were provided with mineral oil. The samples were 40 mm × 40 mm × 160 mm prisms. The casted composite samples were unmolded after 24 h and left to cure for 27 days at laboratory at T = (23 ± 2) °C, RH = (50 ± 5%).

2.2. Methods

The individual methods used are described in detail in the Supporting Information file. The chemical composition of PW, sand and MgO was determined by XRF (X-Ray fluorescence, PANalytical, Almelo, Netherlands). Phase composition of PW was studied by X-ray powder diffraction (XRD, Bruker AXS GmbH, Karlsruhe, Germany) [31]. The morphology was studied by scanning electron microscopy (SEM, Tescan Lyra 3 dual beam microscope, Tescan Brno, s.r.o., Brno, Czech Republi) [32]. Specific density, loose bulk density, and Blaine fineness of MgO, silica sand, and PW were also tested. For the specific density assessment, an automatic helium pycnometer was used. The particle size distribution of PW was analyzed by laser diffraction, while the grain size distribution of silica sand was determined in the standard sieve test. The workability of fresh mixtures was verified using a flow table test.

The hardened composites were tested after 28 days maturing under laboratory conditions. Phase composition was tested on MOC/PW pastes only as the silica peaks would overlap the XRD peaks of precipitated MOC phases. X-ray powder diffraction of MOC/PW pastes was performed similarly as in the analysis of PW. The structural parameters and mechanical resistance of MOC composites were investigated [33]. Mercury intrusion porosimetry (MIP) was used for the detailed investigation of the pore structure of hardened composites. The hygric parameters of developed composites were determined as originally introduced in our previous publication [34]. Among thermal parameters of composites, dry thermal conductivity λ (W∙m⁻²∙K⁻¹), thermal diffusivity a (m²∙s⁻¹), and volumetric heat capacity c_v (J∙m⁻³∙K⁻¹) were tested. The simultaneous thermal analysis (STA) of the matured materials and their FT-IR (VERTEX 70 FT–IR, Bruker Corporation, Mannheim, Germany) analysis were also conducted.

3. Results and Discussion

The chemical composition of quartz sand, porcelain waste (PW), and MgO measured in XRF analysis is introduced in

Table 2. Chemical composition of caustic MgO, quartz sand, and PW (wt. %).

Substance	MgO	Quartz Sand	PW
SiO2	3.8	96.3	63.9
CaO	5.2	-	0.5
Al2O3	6.0	3.1	29.3
MgO	80.5	0.4	0.5
Fe2O3	3.8	-	1.1
K2O	-	-	2.3
SO3	0.4	-	-
Na2O	-	-	1.9
TiO2	-	0.1	0.3
P2O5	-	-	-

. Based on XRF measurements, the main oxides forming the studied materials were detected. For PW, the prevailing constituents were SiO₂ and Al₂O₃ that represented 93.2 wt. % of porcelain waste.

The phase analysis of PW was studied using XRD. The two main crystalline phases that were present in the sample were identified as silicon oxide (ICDD 01-070-3755) and mullite (ICDD 01-074-4143). Also the amorphous background was obtained, due to the presence of glassy SiO₂ with alkali admixtures. Obtained results are shown in Figure S1 (Supporting Information).

SEM micrographs were acquired to study the microstructure and particle size of the porcelain waste (PW). While some particles have a few microns in diameter, other particles had diameters higher than 50 µm. Particle size distribution was also measured by laser diffraction. The EDS was also measured to obtain the chemical composition of PW. EDS detected the presence of Si (35.3 wt. %), Al (12.9 wt. %), O (44.7 wt. %), K (3.5 wt. %), C (2.0 wt. %), and Na (1.4 wt. %). SEM images together with EDS results are depicted in Figure S2 (Supporting Information).

Data provided by laser particle size distribution analysis is presented in Figure 1. For comparison, particle size distribution of used sand measured by the standard sieve analysis is also presented. Porcelain waste was greatly finer in comparison with quartz sand. The particle size distribution parameters of porcelain waste were d₁₀ = 19.9 μm, d₅₀ = 59.3 μm and d₉₀ = 118.9 μm.

Specific density, loose bulk density, and Blaine fineness of MgO, quartz sand, and PW are summarized in

Table 3. Basic physical parameters of MgO, quartz sand, and porcelain waste.

Material	Loose Bulk Density (kg∙m−3)	Specific Density (kg∙m−3)	Blaine Specific Surface (m2∙kg−1)
MgO	843	3337	698
Quartz Sand	1663	2651	-
Porcelain Waste	1164	2506	304

. The highest specific density exhibited MgO which possessed also the higher Blaine specific surface. Porcelain waste had greatly lower loose bulk density compared to quartz sand that was the result of its presumed porosity.

The basic structural parameters of hardened samples and workability characterized by spread diameter are introduced in

Table 4. Basic structural characteristics of MOC composites.

Material	Spread Diameter (mm)	Bulk Density ρb (kg·m−3)	Specific Density ρs (kg·m−3)	Porosity φ (%)
MOC-Ref	165/165 ± 5	2123 ± 30	2436 ± 29	12.8 ± 0.3
MOC-SPW5	175/175 ± 5	2163 ± 30	2262 ± 27	4.4 ± 0.1
MOC-SPW10	160/160 ± 5	2158 ± 30	2241 ± 27	3.7 ± 0.1
MOC-SPW15	140/140 ± 5	2143 ± 30	2236 ± 27	4.2 ± 0.1

. Despite the assumed higher specific surface of PW compared to quartz sand, its 5% replacement with porcelain waste slightly improved the workability of prepared composite mortar which was a consequence of the improved packing density and thus rheology of the fresh mixture. On the other hand, for higher replacement ratio of sand with PW, the spread diameter decreased and thus the workability of composites was worse than that obtained for control material MOC-ref. This was due to the higher dosage of PW and its high specific surface which partially blocked the batch water molecules within samples mixing. In comparison with control composite MOC-Ref, the values of specific density were lower for all MOC composites with sand replacement. The differences were typically ~7–8%. This was in agreement with the observed porosity of these materials, which was much lower compared to control composite. Surprisingly, the lower workability of MOC-SPW10 and MOC-SPW15 had no negative influence on their final porosity as its differences were for materials with PW low, especially taking into consideration the expanded combined uncertainty of porosity test. Quantitatively, the lowest porosity among tested composites reached material MOC-SP10, whose porosity was of about 71.1% lower than measured for reference composite.

The phase composition of hardened composites was determined using XRD. The results showed the presence of the MOC-518 (Phase 5, 5Mg(OH)₂∙MgCl₂∙8H₂O), magnesium oxide, silicon oxide, mullite and chlorartinite, which was present due to the carbonation of MOC. The obtained diffraction patterns can be seen in Figure 2.

Mechanical resistance of hardened MOC composites was characterized by flexural strength R_f, compressive strength R_c, and Young’s modulus of elasticity E_d. As shown in

Table 5. Mechanical parameters of MOC composites.

Material	Flexural Strength Rf (MPa)	Compressive strength Rc (MPa)	Young’s Modulus Ed (GPa)
MOC-Ref	25.1 ± 0.4	76.7 ± 1.2	40.5 ± 0.9
MOC-SPW5	24.7 ± 0.3	74.3 ± 1.0	40.1 ± 0.9
MOC-SPW10	26.8 ± 0.4	85.5 ± 1.2	42.5 ± 1.0
MOC-SPW15	25.6 ± 0.4	77.5 ± 1.1	41.3 ± 1.0

, all samples reached high compressive strength which is usual for this type of material [11,35] and enables its application in load bearing structures. Both flexural and compressive strength were even higher than observed for 28 day samples of typical ordinary PC concrete by Chen et al. [36]. The highest mechanical resistance exhibited material MOC-SPW10. This was assigned to its lowest porosity and presumed activity of PW components with products of MOC precipitation, such as with Mg(OH)₂. On the contrary, 5% silica sand replacement with PW resulted in a drop in all examined mechanical parameters. However, the decrease in mechanical resistance was not significant and was assigned to the lower strength of ceramic waste compared to quartz sand. Also, 15% replacement of quart sand gave material with high mechanical strength and elastic modulus. High flexural/compressive strength ratio (32.7 for MOC-Ref, 33.2 for MOC-SPW5, 31.3 for MOC-SPW10, and 33.0 for MOC-SPW15) and high Young’s modulus are also typical functional properties of MOC composites [37]. The high flexural compressive ratio was typically higher that reported for ordinary PC concrete which is usually in the interval from 0.1 to 0.2 [38].

Figure 3 presents the cumulative pore volume curves of studied samples obtained by MIP analysis. Additionally, the parameters of pore size distribution are summarized in

Table 6. Parameters of pore volume distribution.

Pore Diameter Range (µm)	Specific Vol. (cm3/g)	Specific Vol. (%)	Relative Vol. (%)
MOC-Ref
100–10	0.00936	18.59	18.59
10–1	0.01542	30.60	12.01
1–0.1	0.02186	43.40	12.80
0.1–0.01	0.04845	96.18	52.78
0.01–0.001	0.05027	99.79	3.61
MOC-SPW5
100–10	0.00382	11.28	11.28
10–1	0.01242	36.67	25.39
1–0.1	0.01837	54.24	17.58
0.1–0.01	0.03090	91.24	37.00
0.01–0.001	0.03372	99.55	8.31
MOC-SPW10
100–10	0.00109	3.44	3.44
10–1	0.00803	25.42	21.98
1–0.1	0.01470	46.56	21.14
0.1–0.01	0.02854	90.37	43.81
0.01–0.001	0.03153	99.83	9.46
MOC-SPW15
100–10	0.00149	4.44	4.44
10–1	0.00871	25.94	21.51
1–0.1	0.01432	42.65	16.71
0.1–0.01	0.02914	86.82	44.17
0.01–0.001	0.03355	99.95	13.13

.

The cumulative pore volume curves followed the trend of the total open porosity of tested materials introduced in Table 4. Taking into account the mass of MIP samples and measurement uncertainty, the MIP data were in a good qualitative and quantitative agreement with that obtained based on gravimetric and helium pycnometry tests. It can be seen that the presence of PW in the composition of composites led to a significant decrease of the pore volume in comparison with the reference material. The specific volume of pores in MOC-SPW 5, MOC-SPW10 and MOC-SPW15 decreased to 67.1%, 62.7% and 66.7% of MOC-Ref value, respectively. As regards the pore size terminology in MOC-based composites, individual papers vary. Li et al. [39] stated that volume fraction of pores with diameter >0.1 µm (large pores) is responsible for mechanical properties while pores with diameter <0.1 µm (small pores) affect mainly the water resistance. In our case, MOC-Ref sample exhibited the highest volume proportion of both small and large pores. After the addition of PW into the mixture, the volume of large pores as well as of small pores decreased. In this sense the data obtained by MIP confirmed that modification of composites composition by PW can optimize the pore structure of MOC-based structure, which resulted in the improvement of both mechanical parameters and water resistance.

Parameters characterizing liquid water transport in studied MOC composites are presented in

Table 7. Hygric parameters of MOC composites.

Material	Water Absorption Coefficient Aw ×10−3 (kg m−2·s−1/2)	Sorptivity Sw × 10−6 (m·s−1/2)	Moisture Diffusivity κapp (m·s−2) × 10−9	24 h Water Absorption Wa (%)
MOC-Ref	6.1 ± 0.14	6.1 ± 0.14	4.2 ± 0.2	2.58 ± 0.03
MOC-SPW5	1.8 ± 0.04	1.8 ± 0.04	2.9 ± 0.1	1.35 ± 0.02
MOC-SPW10	1.1 ± 0.03	1.1 ± 0.03	1.5 ± 0.1	1.25 ± 0.02
MOC-SPW15	1.6 ± 0.03	1.6 ± 0.03	2.5 ± 0.1	1.32 ± 0.02

. Application of PW resulted in a notable drop of water absorption rate which was associated with the reduction of porosity and lower pore size. The water absorption coefficient A_w was reduced by 70.3% for MOC-SPW5, 73.6% for MOC-SPW10, and 82.1% for MOC-SPW15 respectively. Similarly, the sorptivity was reduced. The 24 h water absorption W_a was 52.3% (MOC-SPW5), 48.4 (MOC-SPW10), and 51.2% (MOC-SPW15) of the reference value. The apparent moisture diffusivity was also greatly reduced. As the water transport was significantly decelerated and limited by the use of PW in the composition of developed composites, their water resistance and thus durability was improved which is beneficial for application of these advanced materials in construction practice.

Thermal parameters characterizing the ability of studied composite materials to transport and store heat are given in

Table 8. Thermal characteristics of MOC composites.

Material	λ (W·m−1·K-1)	a × 10−6 (m2·s−1)	cv (MJ·m−3·K−1)
Silica sand	0.5	1.7	0.3
PW	0.2	0.5	0.3
MOC-Ref	3.2	1.5	2.1
MOC-SPW5	3.3	1.5	2.2
MOC-SPW10	3.2	1.5	2.1
MOC-SPW15	3.0	1.4	2.1

. Before testing, specimens were dried in a vacuum chamber at temperature 60 °C until their steady state mass was reached. For the explanation of measured data, information on thermal parameters of quartz sand and PW is also provided. While the reference sample reached thermal conductivity of 3.17 W·m⁻¹·K⁻¹, the thermal conductivity of material with 5% replacement of sand slightly increased by 3.5%. Surprisingly, with a higher replacement ratio the thermal conductivity drop continued despite the fact that the lowest porosity was recorded for MOC-SPW10. This materials’ thermal performance was attributed with much lower thermal conductivity of porcelain waste compared to quartz sand. As the porosity of all researched materials was low, this effect predominated over the porosity contribution to the total thermal conductivity and thus thermal diffusivity. The volumetric heap capacity was almost similar for all examined composites as the differences in heat storage were for both fillers low. Although MOC has been known since 1867, very few researchers have focused on the thermal characteristics of this type of material. Certain exception represent studies [36,40], where authors tested MOC-based materials with silica sand aggregate and bulk density of ~2100 kg·m⁻³. They reported on the thermal conductivity of MOC composites in the range of 2.1–2.2 W·m⁻¹·K⁻¹, which was lower compared to the thermal conductivity values presented in this paper.

The collected FT-IR spectra (Figure 4) of tested magnesium oxychloride cement composites show the absorption bands between 400–800 cm⁻¹ which can be attributed to the stretching and bending vibrations of Si-O, Al-O, Mg-O, and Mg-Cl of the lattice, while the absorption band at 845 cm⁻¹ can be assigned to the characteristic absorption peak of Mg-O in cubic structure [13,41]. The absorption band at 1021 cm⁻¹ is typical for stretching vibration of Si-O mode of magnesium silicate hydrate [42]. The absorption bands near the 1600 cm⁻¹ are caused due to H₂O bending mode vibration in MgCl₂∙8H₂O. The absorption band at 1149 cm⁻¹ and stronger at 1423 cm⁻¹ are attributed to the stretching vibration of C=O in carbonates, resulting from the presence of MgCO₃ in light burned magnesia and from the carbonation reaction [43]. The spectral range around 2000 cm⁻¹ includes a lot of absorption bands coming from the bending and rocking vibrations of O-H in H₂O and (Mg(OH)₂) and also carbonates overtones. As the intensities of these absorption bands were low, they were not analyzed in detail. The absorption bands in the range of 3300–3700 cm⁻¹ are contributed by the symmetric and asymmetric stretching mode of O-H bonds in H₂O and Mg(OH)₂ [42]. These are reduced after adding the porcelain waste due to inhibition the formation of Mg(OH)₂ in hardened MOC composites. It is believed to leads to improve the mechanical parameters of composites with PW [42].

Thermal behavior of the investigated materials at high temperatures was studied using STA (Figure 5). All analyzed samples showed very similar behavior; the overall weight decrease was in the range between 29.6 wt. % to 33.9 wt. %. A slightly lower value was obtained for the sample MOC-SPW-15 with the highest PW content, which was caused due to high thermal stability of the phases present in PW. In all samples, the gradual decomposition of phase MOC-518 was obtained, that was already described in the literature [44,45]. During the heating, eight water molecules were released from 5Mg(OH)₂∙MgCl₂∙8H₂O to 300 °C. Further heating led to the complete decomposition of this phase forming MgO. This process was associated with the release of water and hydrochloric acid [13].

4. Conclusions

Combination of laboratory processed porcelain waste and natural quartz sand was used as a blended filler of MOC composites. The developed materials were characterized by their structural, parameters and hygrothermal performance together with the analysis of their phase composition and thermal stability. As MOC is low carbon binder it can potentially represent an interesting alternative for Portland cement-based materials whose production enormously depletes natural resources and excessively generates greenhouse gases. The performed experiments and acquired data allowed to draw the following conclusions:

• a 5% substitution of silica sand with PW moderately improved workability of fresh mixture, but the spread diameter of composites with a higher dosage of PW was slightly lower than that measured for control mixture MOC-Ref;
• the usage of waste porcelain greatly decreased the porosity of composite matrix;
• the drop in porosity resulted in high mechanical resistance and reduced and decelerated water imbibition;
• the 10% sand substitution with PW brought the best mechanical resistance and the lowest water absorption due to the formation of amorphous phases (undetectable by XRD) from the reaction between precipitated MOC products (presumably Mg(OH)₂) and PW forming phases which are partially reactive, the results are hydrated water insoluble aluminosilicates;
• in case of the thermal performance of the examined composites, the low thermal conductivity of PW was the contradictory parameter to porosity;
• due to high thermal stability of the phases present in PW, the thermal decomposition of composites slightly decreased with PW dosage.

It can be concluded that the partial substitution of quartz sand in MOC composites enabled materials possessing interesting and advanced function and technical parameters to develop. The assessed materials’ properties can be further exploited in design and production of high-performance construction materials with specific application potential. The main benefits of the developed composites are low carbon footprint, low porosity that limits the risk of water damage, high mechanical resistance, and application of waste or secondary raw material (PW) in their composition. Moreover, the properties of MOC matrix with sand/porcelain waste filler can be effectively modified, e.g., by the addition of lightweight aggregate which could enhance the thermal insulation behavior of final composites. This will be the objective of future studies.