DOI:10.32604/jrm.2021.012228
| Journal of Renewable Materials DOI:10.32604/jrm.2021.012228 | |
| Article |
Study on Factors Affecting Properties of Foam Glass Made from Waste Glass
1School of Material Science and Engineering, Shanghai University, Shanghai, China
2Huichang New Material Co., Ltd., Xuancheng, China
3Changda Thermal Insulation Technology Co., Ltd., Xuancheng, China
*Corresponding Author: Jianjun Xie. Email: xiejianjun@shu.edu.cn
Received: 20 June 2020; Accepted: 10 September 2020
Abstract: Foam glass is a new green material to make use of waste glass and is popular for its energy-saving and light weight features. The problems in the current study of foam glass is that its properties require improvement to match the growing demands of application specific standards. Properties of foam glass is related to its porous structure, which is affected by various factors. The influence of raw material component, foaming agents and sintering system on the porous structure and properties of foamed glass is studied. Density decreases with the decrease of quartz and barite content. Thermal conductivity is more affected by barite content, and the lowest thermal conductivity is obtained when 10% quartz and 6% borax are added. Compressive strength is more affected by borax content, and the highest compressive strength is obtained when 5% quartz, 10% barite and 6% borax are added. Foam glass samples with different porous structures and improved properties are obtained using graphite and CaCO3 as foaming agents. Compared with the soldcommercial foam glass for thermal insulation materials, the compressive strength of samples prepared by using compound foaming agents is increased by a factor of 2–3 times higher. With porous structure and properties adjusted by the optimization of raw materials and foaming agent, there exists the potential for factories to produce foam glass with expanded application scope.
Keywords: Foam glass; waste glass; orthogonal test; properties
With the continuous promotion of environmental protection policies, green and environmentally friendly materials are more attractive to users in various fields [1–3]. Foam glass, a new green material made from waste, has a highly porous structure (total porosity > 80%). Properties and application of foam glass depend on its pore type. Closed-porous foam glass (open porosity < 10%) applies to building material and has superior performance over traditional thermal insulation materials, including low thermal conductivity (λ < 0.1 W·m−1·k−1), high compressive strength (σ > 0.5 MPa), water resistance and long life-span. Open-porous foam glass (open porosity > 50%) shows good sound insulation and water absorption capability, applying in metro station and gardens.
The main raw materials for foam glass are waste including types of waste glass, fly ash and slag [4–8]. New raw materials for foam glass producing appear in recent years [9,10]. As reported, according to chemical composition of the raw materials [11], the foaming agent, which releases gas bubbles in the softened glass or a slag powder to form a porous structure, is selected to match the thermal properties of the raw materials. Of all the published decomposition and redox reaction type foaming agents, black carbon is the most commonly used and the gas released (CO2) by it has a lower thermal conductivity than N2 and O2 [12,13]. Different raw material components, foaming agents, auxiliary agent types, and sintering or annealing process all lead to a different porous structure and foam glass performance. Apart from low apparent density, foam glass with predominantly closed pores exhibits low thermal conductivity and high water resistance, while that with predominantly open pores exhibits excellent acoustic insulation.
Despite the fact that foam glass appeared in the 1940s, companies and literature reports only began to grow substantially in the past 10 years. With the rapid development of foam glass industry, the problems of overcapacity and backward performance have emerged. Recently, foam glass is mainly used as a thermal or acoustic insulation material because of its highly porous structure [14]. Compared with traditional thermal insulation materials, foam glass has a much longer lifespan resulting from its chemical and thermal stability. However, compressive strength should also be considered in all application fields [15]. The compressive strength of foam glass is related to its porous structure, which is affected by a large number of factors [16,17]. Firstly, due to the difference between foaming temperatures of various foaming agents [18,19], the viscosity of the melt during the foaming stage differs [20], thus, the resulting resistance to pore growth differsAdditionally, particle size affects the uniformity of the foaming agents in the mixture and the severity of the foaming reaction [12]. Inhomogeneous dispersion of the foaming agent and an incomplete foaming reaction lead to a non-uniform porous structure foam glass with reduced compressive strength [21]. Further, during the foam glass sintering process, pore coalescence is enhanced by prolonging the holding time or increasing the cooling rate [4], forming a predominantly open-porous distribution, which leads compressive strength to decrease.
Since the formation of foam glass is complex, the understanding of factors affecting structure and properties of foam glass makes it possible that porous structure and properties of foam glass are adjusted to meet different application standards. The present work is twofold: (i) To study the influence of raw material content on structure and properties of foam glass by the orthogonal test. Considering quartz sand, barite and borax content as the main factors, an orthogonal experiment having three factors divided into three levels is designed. (ii) To study the influence of different types of foaming agentson structure and properties of foam glass. Graphite is a redox foaming agent, which can produce gas continuously during the heating process, and is likely to form a closed-porous structure [18]. CaCO3 is a decomposition foaming agent, which decomposes at high temperature, producing large volumes of gas, and is thus likely to form an open-porous structure [22]. CaCO3 is added to couple with graphite to form compound foaming agents. By altering the raw material content, proportion of compound agents, and the foaming temperature, the pore structure of foam glass can be adjusted and its properties optimized. Thus, the performance requirements of foam glass in different service fields can be met, expanding the application scope of foam glass.
Waste glass was crushed into pieces by a hammer and subsequently ball milled with ethanol in a planetary ball for 3 hours at 200 rpm. The obtained powders were then dried for 2 hours. Graphite (CP, Sinopharm) and calcium carbonate (CP, Sinopharm) were added to the fine glass powder and were ball milled at 150 rpm for 45 min. Graphite and CaCO3 powders were ball milled first to form big aggregate before added to the whole mixture,their main reactions during foaming process are listed below. The powder mixtures were placed in a stainless steel mold coated with a release agent and heated at 10°C/min to different foaming temperature. Subsequently, the sample was cooled at 5°C/min to the glass transition temperature and then naturally cooled to room temperature. Obtained sample was processed to square shape and kept in oven.
Waste glass powder was heated to 300°C to eliminate polymer impurities and then the chemical composition of the float glass powder was obtained by chemical analysis with an X-ray fluorescence spectrometer (XRF-1800, SHIMADZU LIMITED, Japan).
The morphology of foam glass was examined using a scanning electron microscope (SEM) operating at 15 kV (Nova NanoSEM 450, FEI, CZ). SEM measurements were performed on powder mixtures coated with Au.
X-ray diffraction analysis (XRD) was performed with an X-ray diffractometer 3KW D/MAX2200V PC (Riken Electric Co., Ltd., Japan).
To investigate the thermal activities of foaming agents during the heating process, differential scanning calorimetry (DSC) and thermogravimetry (TG) measurements were performed using a synchronous thermal analyser 404C instrument (NETZSCH-Gerätebau GmbH, Germany).
Shown in Fig. 1, the thermal conductivity of the prepared samples (12 × 12 × 1.5 mm3) at room temperature was investigated using the transient hot line method (TC3000E, XIATECH, China). For this purpose, the sensor is sandwiched between two flat test specimens and pressed with a 500 g weight to reduce the thermal contact resistance generated by air. The sensor was electrically heated by applying a specific constant heating power at 0.5–4.5 V over a defined measuring time of 1–30 s [9]. By measuring the increase in the electrical resistance, the temperature increase of the wire was determined, which is directly related to the thermal conductivity of the sample [18]. Theoretical calculation formula of thermal conductivity model for foamed glass is [23]:
Figure 1: Picture of sensor for transient hot line method
λs—thermal conductivity of basic glass
Ps—volume of glass phase
λp—thermal conductivity of gas
Pp—volume of gas phase
The compressive strength of the prepared samples (12 × 12 × 1.5 mm3) was investigated with a universal material testing machine (JWE-50, China). The true density (ρt) was determined by Archimedes’ principle using a complete float glass block. The apparent densities (ρapp) of the small samples were determined by Archimedes’ principle using a density weighing balance. The apparent density (ρapp) of the large samples was calculated from the mass and dimensions of the sample [24]. Additionally, the percentages of total porosity (TP), open porosity (OP) and closed porosity (CP) were calculated from m1 (dry weight), m2 (wet weight), m3 (absorbed water weight).
Theoretical calculation formula of strength model for porous materials is [25]:
R—strength of porous materials
Ro—strength of solid materials
Zh—constant determined by pore size
m—number of pores
k—ratio of major axis to minor axis of ellipsoidal hole
p—pore size
Vp—volume of gap
The mean pore size and pore size dispersion were calculated from the macrostructure of the prepared samples using analysis software (Nanomeasure). The calculation process is shown in Fig. 2.
Figure 2: Nanomeasure software calculation process
As shown in Tab. 1, waste glass has a large amount of CaO and Na2O content, which reduces the melting point. When quartz and barite are added, increase of high melting point component enhance the lattice strength of glass, making bubbles more stable during sintering process.
Table 1: Raw material chemical composition determined by X-ray fluorescence
TG-DSC result of waste glass is shown in Fig. 3. Since Tg of waste glass is around 700°C, CaCO3 (start to generate CO2 at around 800°C) and graphite (start to generate CO2 at around 600°C) is used in the present work, which better fits the muffle furnace’s intermittent heating program features and avoid the leak of CO2 during the pre-sintering stage (400°C–550°C).
Figure 3: Thermogravimetry-differential scanning calorimetry (TG-DSC) curves of waste glass
Apart from difference of raw material and borax content, Sample (a)-(i) are all made by CaCO3 foaming agents sintered at 850°C. Density, thermal conductivity and compressive strength values are listed in Tab. 2.
Table 2: Orthogonal test results of combined raw materialsa
aTotal mass of waste glass, quartz and barite is 5 g (100%). λ is thermal conductivity. σ is compressive strength.
The range analysis result is listed in Tab. 3.
Table 3: Range analysis of orthogonal test results
Fig. 4 is based on kj value in Tab. 3. As Fig. 4 shows, According to the thermal conductivity and strength model of porous materials, thermal conductivity increases with glass phase volume, while compressive strength increases with uniform porous structure and decrease of gap volume when total porosity remains unchanged. With the increase of quartz content (0–5%), density and open porosity increases slowly, while thermal conductivity and compressive strength decrease, indicating that uniformity decreases and gap volume increases with increase of open porosity. With more quartz added (5%–10%), increase of glass phase and growth resistance lead to the increase of thermal conductivity and compressive strength and decrease of open porosity. Density, thermal conductivity and compressive strength increase with barite content, but open porosity decreases when barite increases from 5% to 10%, indicating the collapse of big pores. With the increase of borax content (decompose to Na2O and B2O3 at high temperature), fluxing effect of Na2O and enhancement of glass lattice strength by B2O3 lead to the decrease of density and open porosity.
Figure 4: Curve of range analysis of orthogonal test results
It can be seen from Tab. 4 that the F of the three factors is below the critical value of density, thermal conductivity and compressive strength. Comparing F values, quartz has the greatest influence on density and borax has the greatest influence on thermal conductivity and compressive strength.
Table 4: Variance analysis of orthogonal test results
Therefore, when preparing foam glass for use of thermal insulation material, barox content is considered first to get a uniform porous structure and fine thermal and mechanical properties. Quartz and barite content are considered second to get a lower density and higher compressive strength.
3.3 Micromorphology of Foam Glass Samples Made by Combined Raw Materials
It can be seen from Fig. 5 sample (a) and (b) that a few large pores are surrounded by a number of small pores. These small pores are referred to as a bubble band because of their bubble like features and continuous distribution [16]. In the process of bubble growth, the existence of bubble bands reduces the gap volume, thus, enhances the strength of large pores Sample (a) has an inhomogeneous porous structure and the bubble band is cut off by large pores. An indentation within a large pore is seen in samples (b) and (i), but no coalescence of pores has occurred. Sample (c) and (h) show a homogeneous porous structure with thick pore walls, while pore walls are thin and sharp in samples (d) and (e). Coalescence and collapse of pores are evident in samples (e) and (f). Sample (h) has the highest compressive strength of 5.16 MPa. The SEM micrograph shows a homogeneous porous structure with thin pore walls.
Figure 5: SEM micrographs of foam glass samples made using combined raw materials. All scale bars 100 μm
3.4 XRD Analysis of Foam Glass Samples Made by Combined Raw Materials
The results (Fig. 6) show that the diffraction peak of quartz is very weak in sample (a), in which only waste glass is used. When the ratio of quartz sand and barite added to the raw materials is 1:1, a high intensity quartz peak is seen in samples (b) and (c). The raw materials of sample (g) and sample (f) are waste glass and barite. A high intensity BaSO4 peak is seen in sample (g), indicating that increase of borax from 4% to 6% lead to the crystallization of BaSO4.
Figure 6: X-ray diffraction patterns of foam glass prepared from combined raw materials
Based on the above results, the optimal raw material proportions for subsequent experiments are 95% waste glass, 5% quartz and 2% borax.
3.5 Micromorphology of Foam Glass Samples Made by Compound Foaming Agents
Figs. 7a and 7b are micrographs of foam glass samples prepared with graphite foaming agents. Fig. 7b shows that there are some tiny pores inside larger pores, indicating that growth resistance differs in different directions. Fig. 7d shows that when CaCO3 is added, most pores grow bigger and large pores surrounded by bubble band are mostly closed. Fig. 7c shows that when more CaCO3 is added, the wall between pores becomes too thin for bubble bands to exist, and most pores are connected which leads to a decrease in compressive strength.
Figure 7: SEM micrograph of foam glass sample section for (a), (b) 1% graphite, (c) 1% graphite and 2% CaCO3 and (d) 1% graphite and 1% CaCO3. Micrographs not to the same scale
3.6 XRD Analysis of Foam Glass Samples Made by Compound Foaming Agents
As the XRD analysis results of Fig. 8 show, a sharp graphite diffraction peak (2θ = 26.546°) is detected when the foaming agent is 1% graphite. This is because when the mixture is heated above the glass transition temperature, the graphite particles are gradually surrounded by the liquid phase, and the oxygen between the particles is not sufficient to allow the graphite to react completely. With the addition of CaCO3, which decomposes at high temperature and releases a large amount of CO2, residual graphite is consumed through reaction (1–3), resulting in a weak graphite diffraction peak. As the content of CaCO3 is increased from 1% to 3%, the graphite diffraction peak is unchanged, but an enhancement of the silicon oxide diffraction peak (2θ = 30.104°) was observed. This may be the superposition of the CaSiO3 diffraction peak (2θ = 29.975°) and the silicon oxide diffraction peak, caused by some of the aggregate CaCO3 following reaction (1–5), and crystallization of CaSiO3 occurring.
Figure 8: X-ray diffraction patterns of foam glass prepared with compound foaming agents
3.7 Effect of Foaming Agent Content and Foaming Temperature on Pore Structure of Foam Glass Samples
Fig. 9 shows that the total porocity of foam glass samples increases slowly as the amount of graphite is increased and as the foaming temperature is increased. The TG-DSC curve (Fig. 3) shows that Tg of waste glass is 737.66°C. Graphite starts to react at about 600°C when the glass matrix is not completely melted and CO2 can easily escape. Additionally, the oxygen content in the pores of the glass matrix is low at high temperature, and graphite is relatively stable and difficult to oxidize. Thus, the low expansion of foam glass leads to a low total porocity. For compound foaming agents, the total porocity of the foam glass samples increased rapidly. With the increase of CaCO3 content and foaming temperature, the sample total porocity further increased to 90.13%. This is because the decomposition of CaCO3 at high temperature produces large amounts of CO2, and CaO breaks the tetrahedral structure of SiO2 to reduce the resistance of pore growth [24].
Figure 9: Total porosity as a function of foaming agent content and foaming temperature
As shown in Fig. 10, even for increased foaming temperature and foaming agent content, the porosity of foam glass prepared by a single foaming agent remains at 70%–80%. When graphite and CaCO3 are used in combination, closed pores decrease from 80% to 10% porosity. This is a practical means to adjust the closed porosity of foam glass, meeting the requirement of different application fields [14,26].
Figure 10: Closed porosity of foam glass samples as a function of foaming agent content and foaming temperature
It can be seen from the foam glass pore distribution map (Fig. 11) that the mean pore size of foam glass prepared using a single foaming agent is small, and the pore growth is not related to the increase of graphite content and foaming temperature. The proportion of pores below 1 mm decreased, and the mean pore size of foam glass increased with the increase of CaCO3 content.
Figure 11: Pm (mean pore size) of foam glass made using different foaming agents
3.8 Effect of Foaming Agent Content and Foaming Temperature on Thermal Conductivity and Compressive Strength of Foam Glass Samples
It can be seen from Fig. 12 that increasing the foaming agent content and foaming temperature reduces the thermal conductivity of foam glass, and that the thermal conductivity is more sensitive to the change of foaming temperature than foaming agent content. The thermal conductivity of foam glass prepared using a compound foaming agent meets the thermal performance requirements of insulation material. The obtained lowest thermal conductivity is 0.0516 (W·m−1K−1), which is lower than that of commercial foam glass. With increasing of CaCO3 content, the rate of change of thermal conductivity decreases. This is because increasing the number of open pores leads to an increase of gas flow heat transfer and gas-solid convection heat transfer [4]. Thus, in order to obtain further decrease of thermal conductivity, a larger closed porosity must be achieved without decreasing the total porosity.
Figure 12: Histogram showing effect of foaming agent content and temperature on thermal conductivity of foam glass samples
It can be seen from Fig. 13 that graphite plays an important role in increasing the compressive strength of foam glass when using compound foaming agents. Samples made using 1% graphite coupled with 2% or 3% CaCO3 at 850°C, have a thermal conductivity close to that of commercial foam glass but with a 59%–169% increase in compressive strength.
Figure 13: Histogram showing effect of foaming agent content and temperature on compressive strength of foam glass samples
In summary based on the above experiments we conclude:
i) According to the results of the orthogonal test, porous structure and properties are adjusted by change of raw materials. It is practical to improve foam glass quality used as thermal insulation materials. barox content is considered first to get a uniform porous structure and fine thermal and mechanical properties. Quartz and barite content are considered second to get a lower density and higher compressive strength.
ii) CO2 produced by decomposition of CaCO3 at high temperature reacts with graphite, making the oxidation of graphite more complete to increase growth motivate power of pores. The residual graphite is distributed on the phase interface of gas and liquid phase, which reduces the interface energy and stabilize the pores, thus, foaming a highly porous structure with good compressive strength. Foam glass with optimized performance is obtained by 1% graphite and 2% CaCO3 at 850°C, which exhibits insulation performance (λ = 0.0661W·m−1·k−1) as good as commercial foam glass with much better mechanical performance (218% improvement).
iii) With the increase of CaCO3 content, porous structure changes from closed-porosity to open-porosity. It is practical for foam glass to meet application specific porous structure requirements, such as those of sound insulation materials and water storaging materials.
Acknowledgement: We thank engineer Gu Feng for support of density and pore structure measurement. We thank Bambie bei for help of graphic processing. We also thank Dr Ding Mao Mao and Yuan Rui for help of compressive strength and thermal conductivity measurement.
Funding Statement: This work was supported by the Shanghai Municipal Natural Science Foundation, China (No. 19ZR1418500) and National Natural Science Foundation of China (51172139).
Conflicts of Interest: The authors declare that they have no conflicts of interest to report regarding the present study.
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