Effect of sintering additives on the densification

Materials Chemistry and Physics 216 (2018) 1–7

Contents lists available at ScienceDirect

Materials Chemistry and Physics journal homepage: www.elsevier.com/locate/matchemphys

Effect of sintering additives on the densification, crystallization and flexural strength of sintered glass-ceramics from waste granite powder

T

Jinshan Lua,b,∗, Yingde Lia, Chuanming Zoua, Zhiyong Liua, Chunlei Wangb a b

School of Materials Science and Engineering, Nanchang Hangkong University, Nanchang 330063, China College of Engineering and Computing, Florida International University, FL 33174, USA

H I GH L IG H T S

G R A P H I C A L A B S T R A C T

boehmite was preferable for the • The densification and strengthening. crystallinity decreased with in• The creasing the sintering temperature. crystallinity increased with in• The creasing the boehmite content. flexural strength depended on • The densification and crystallinity.

A R T I C LE I N FO

A B S T R A C T

Keywords: Granite powder Sintering additive Glass-ceramic Crystallinity Flexural strength

Large amounts of granite wastes in the stone processing industry should be recycled to prevent the environmental pollution and health hazards. In this work, the sintered glass-ceramics have been prepared from granite powder by the sintering-crystallization method. The sintering additives were investigated to reveal their influence on the densification, crystallization and flexural strength of glass-ceramics. Compared to colloidal silica and float glass powder, the boehmite sol was more effective in the strengthening of glass-ceramics. The crystallinity of glass-ceramics decreased with increasing the sintering temperature due to the melting of microcline phase, and the microstructure was typical of liquid phase sintering. The crystal phases included anorthite, quartz and hematite. As the boehmite content was increased, the flexural strength firstly increased and then decreased, showing an optimal content of 3 wt%. The maximum flexural strength (125 MPa) was far superior to that of natural granite. The crystallinity continuously increased with the increase in the boehmite content. The sintered glass-ceramics with decorative patterns and high flexural strength promise the practical reutilization of granite wastes in the ornamental tiles.

1. Introduction For the granite production and consumption, China has been one of the main countries in the world. The gross production of granite slabs amounts to 730 million square meters in 2016 [1]. Being ∼60% of the granite blocks, granite wastes should be properly disposed to prevent the environmental pollution and health hazards [2,3]. The reutilization

∗

of granite wastes not only gets rid of the environmental problems, but also ensures the sustainable granite exploitation [4]. The granite wastes have been usually recycled into the construction and building products to reduce the consumption of natural minerals [5,6]. They were incorporated in the cements and concretes as the aggregate, filler and mineral additive without the detrimental effects on the workability, water absorption and durability. With the feldspar

Corresponding author. School of Materials Science and Engineering, Nanchang Hangkong University, Nanchang 330063, China. E-mail address: [email protected] (J. Lu).

https://doi.org/10.1016/j.matchemphys.2018.02.053 Received 29 December 2017; Received in revised form 2 February 2018; Accepted 9 February 2018 Available online 30 May 2018 0254-0584/ © 2018 Published by Elsevier B.V.


J. Lu et al.

constituents, granite powder was used as the fluxing agent in the porcelain tiles and ceramics [7,8]. In addition, granite wastes were applied in the treatment of wastewater sludge, acid soil and radioactive waste [9–11]. Regarding the profitable reutilization, granite wastes are promising in such applications as glaze and glass-ceramics. When the diopside glaze was prepared from glass-ceramic frit and granite waste, the iron content played a crucial role in controlling the crystalline composition, crystallization and glaze appearance [12]. Transparent and opaque glazes from the combination of float glass, granite and lime shale exhibited the comparable hardness and corrosion/abrasion resistance to that of commercial glazes [13]. With the addition of other chemicals/ minerals, the glass-ceramics could be prepared from granite wastes by the melting-crystallization method, exhibiting the excellent mechanical properties [14,15]. Unlike the common melting-crystallization process, the sintered glass-ceramics were simply prepared by the simultaneous sinteringcrystallization process from the powder mixtures [16]. In this work, the modified granite powders were directly sintered into high strength glass-ceramics. The sintering additives were investigated to reveal their influence on the densification, crystallinity and flexural strength of glass-ceramics. The microstructural evolution was carefully examined to clarify the densification process. The strengthening mechanism of glass-ceramics was discussed in terms of the densification and crystallinity. The decorative glass-ceramic was preliminarily prepared to demonstrate its commercial feasibility in ornamental tiles.

distilled water (1 wt%). After magnetically stirred for 25 min, the hydrolytic solution was mixed with 60 wt% of granite powder in a polypropylene bottle. Afterwards, the sintering additives and zirconia beads ten times the mass of granite powder were added sequentially. The sintering additives were 3 wt% relative to the granite powder, and the boehmite could be adjusted at 0.5–5 wt%. The powder suspension was ground in a planetary ball mill at 300 rpm for 1 h. Finally, the milled slurry was separated from the zirconia beads, dried at 80 °C for 1 h, and passed through a 200-mesh sieve. The powder mixtures were uniformly blended with 20 wt% of PVA solution, and uniaxially pressed in a rectangular mould at 100 MPa for 5 min. The green compacts were thermally treated at 500 °C for 1 h to remove the PVA binder, and sintered in an electrical furnace with a heating rate of 10 °C/min at 1050–1150 °C for 2 h. The sintered glassceramics were ground with SiC papers and polished with diamond paste. 2.3. Characterization and physical properties of glass-ceramics The chemical composition of granite powder was analyzed by the wave length dispersive X-ray fluorescence (S4 PIONEER, Bruker AXS, Germany). The crystal structure of granite powder and sintered glassceramics was examined by X-ray powder diffraction (XRD, D8 Advance, Bruker AXS, Germany) using Cu Kα radiation. The volume percentage of different phases and crystallinity of glass-ceramics were estimated from the XRD pattern simulation using the MDI Jade 6 software [17,18]. The thermal behavior of granite powder was evaluated by the differential thermal analysis and thermogravimetry (DTA/TG, STA 449C, Netzsch GmbH, Germany) with a heating rate of 10 °C/min in an air flow (50 ml/min). The bulk density of glass-ceramics was measured by using the Archimedes' method. The densification of glass-ceramics was observed with an environmental scanning electron microscope (SEM, Quanta 200, FEI, USA). The phase distribution of glass-ceramics was analyzed with the backscattered electron imaging using a field-emission scanning electron microscope (FESEM, Nova NanoSEM 450, FEI, USA), which was equipped with an energy dispersive spectrum analyzer (EDS, Inca 250 X-Max 50, Oxford Instruments, UK). Prior to the SEM and FESEM observations, the sample surfaces were deposited with gold films to improve the electrical conductivity. The flexural strength of glassceramics was measured in the three-point bending tests with a universal testing machine (WDW-50, Jinan Shijin, China). The cross-head speed was kept at 0.5 mm/min. All rectangular samples were 45 mm × 5 mm × 4 mm in size, and were chamfered to eliminate the stress concentration. Each data point represents an average value of at least five individual tests.

2. Materials and methods 2.1. Materials To remove the soluble impurities, grey granite powder from a stone processing factory was washed with distilled water, filtered and dried, and passed through a 120-mesh sieve. The silicane coupling agent of γglycidoxy-propyltrimethoxysilane (Silquest A-187) was selected as the surface modifier of granite powder. The sintering additives included aqueous boehmite sol (γ-AlO(OH), 20 wt%, pH = 4.5), colloidal silica (30 wt%, pH = 9.0) and self-made float glass powder (200 mesh). Analytically pure methanol was purchased from Sinopharm Chemical Reagent Co. An aqueous polyvinyl alcohol solution (PVA, 2 wt%) was used in the powder compaction. Zirconia beads (NanorZr-93, ∅ 2–5 mm) as the milling media were from Guangzhou Pleased Grinding Media Co. 2.2. Preparation of sintered glass-ceramics The processing route of sintered glass-ceramics was schematically illustrated in Fig. 1. In the powder modification process, the modifying solution was prepared with methanol (97 wt%), A-187 (2 wt%) and

3. Results and discussion 3.1. Characterization and thermal behavior of granite powder The granite powder was characterized by the particle morphology, crystal structure and chemical composition. As shown in Fig. 2, microsized particles exhibited sharp edges and cleaved surfaces, characteristic of the brittle and stiff fracture of granite stone. The crystal structure of granite powder consisted of quartz (PDF 46–1045), anorthite (Na0.45Ca0.55Al1.55Si2.45O8, PDF 85–1415) and microcline (KAlSi3O8, PDF 72–1114) phases. The volume percentage of quartz and microcline was estimated as 66% and 11%, respectively. Owing to high similarity in the XRD patterns, the albite phase (K0.2Na0.8AlSi3O8, PDF 83–2215) was hardly discernible from the anorthite phase. An approximate estimation by the difference of minor diffraction peaks resulted in 14% anorthite and 9% albite. Practically, the albite and anorthite phases formed the solid solutions of plagioclase with different proportions [19]. The chemical composition of granite powder is shown in Table 1.

Fig. 1. Schematic illustration of the processing route of sintered glass-ceramics. 2


J. Lu et al.

Fig. 2. Characterization of granite powder. (a) SEM image; (b) XRD pattern.

the sintering additives to promote the densification and strengthening of sintered glass-ceramics. To compare the sinterability, the powder mixtures with 3 wt% sintering additives were sintered at 1100 °C for 2 h. The sintered glass-ceramics were denoted as SM3S (silica), SM3B (boehmite) and SM3G (glass). As a control, the granite powders without (None) and with (SM) surface modification were sintered under the same conditions. Fig. 4 shows the bulk density and flexural strength of sintered glassceramics. The glass-ceramic from pristine powder exhibited a bulk density of 2.40 g/cm3 with a flexural strength of 76 MPa. After surface modification, the bulk density was reduced to 2.37 g/cm3, while the flexural strength (83 MPa) was somewhat increased. When the granite powder was modified with reactive silanol groups, the dehydroxylation of adsorbed silanol groups activated the initial sintering of particles at low temperatures [28], which had an adverse impact on the subsequent liquid phase sintering at high temperatures. Nevertheless, the formation of Si-O-Si bonds contributed to the enhancement of interface adhesion [29]. On the basis of surface modification, the addition of sintering additives slightly improved the densification of glass-ceramics, and the bulk density was increased by 1.2% (SM3S), 2.9% (SM3B) and 0.8% (SM3G). The flexural strength of glass-ceramics varied with the sintering additive. The silica and glass powder resulted in inferior strengths of 74 MPa and 65 MPa respectively, whereas the boehmite presented a superior strength of 114 MPa. Therefore, the boehmite was much more effective in improving the densification and flexural strength of glass-ceramics. The difference in densification could be reasonably interpreted with the filling effect of silica/boehmite and the liquid phase sintering of glass powder. The inert silica filler was detrimental to the interfacial adhesion [30], and the mismatch in the thermal expansion coefficient between soda-lime glass (8.9 × 10−6 K−1 [31]) and granite (4.0 × 10−6 K−1 [32]) could induce the microcracks at the particle interfaces. Accordingly, the addition of silica and glass powder decreased the flexural strength of glass-ceramics. On the other hand, boehmite was thermally decomposed into superfine and active alumina particles [33]. The formation of anisotropic anorthite phase between alumina and glassy phase greatly increased the flexural strength of glass-ceramics.

The abundance of silica and alumina was favorable to the formation of aluminosilicate phases, consistent with the anorthite and microcline phases. Besides, the granite powder contained a small quantity of iron oxide. The iron oxides could exist in various phases and morphologies in the interstices, which were not detectable due to the XRD resolution limit [20]. Fig. 3(a) shows the DTA-TG curves of granite powder. The DTA curve showed a broad exothermic band at 300 °C, presumably due to the oxidation of organic impurities and anionic flocculants in the granite powder [21]. The weak endothermic peak at 580 °C corresponded to the phase transformation of quartz (α→β) [22]. In the TG curve, there were a sharp weight loss (0.35%) at 557–680 °C, a slight weight gain (0.03%) at 680–1025 °C and a weight loss (0.06%) at 1025–1100 °C. The weight loss between 557 °C and 680 °C was related to the removal of interstitial water and dehydroxylation of minerals in the granite powder [23]. Considering the weak exothermic band centered at 950 °C, the slight weight gain at 680–1025 °C should be attributed to the oxidation of metal ions with low valence (e.g. Fe2+) [24]. In addition, the weight loss above 1025 °C stemmed from the elimination of hydroxyl groups in the quartz crystals [25]. To understand the structural evolution, granite powder was calcined at 500 °C, 700 °C, 1000 °C and 1100 °C for 10 min. The XRD patterns of calcined powders were recorded in Fig. 3(b). Below 700 °C, the patterns were basically identical to that of pristine powder. The intensity of microcline phase was greatly increased at 1000 °C because the enhanced diffusion of metal ions promoted the crystallization at elevated temperatures. As the temperature was further increased to 1100 °C, the microcline phase was converted into the glassy phase due to its relatively low melting point (1100–1200 °C) [26]. The anorthite phase (Tm: 1552 °C) gradually increased with increasing temperature, while the quartz phase was obviously decreased at 1100 °C. The partial dissolution of quartz in the glass melt facilitated the nucleation and crystallization of anorthite phases [27]. Similarly, the hematite phase (PDF 89–0599) was precipitated after the formation of glass melt. The relative content of crystal phases was determined as 22% (anorthite), 5% (quartz) and 8% (hematite). Hence, the crystallinity of calcined powder above 1000 °C was significantly decreased due to the formation of glassy phase. 3.2. Effect of sintering additives on the densification and flexural strength of glass-ceramics

3.3. Effect of sintering temperature on the densification and flexural strength of glass-ceramics

In these experiments, the surface modification was intended to improve the uniformity and sintering activity of granite powder, and

In the sintering process, the modified granite powder with 3 wt%

Table 1 Chemical composition of granite powder (wt%). Oxides

SiO2

Al2O3

Fe2O3

K2O

CaO

Na2O

MgO

TiO2

P2O5

SO3

LOI

Content

62.8

15.1

5.7

4.8

4.3

3.4

1.4

0.9

0.6

0.4

0.6

3


J. Lu et al.

Fig. 3. Thermal behavior of granite powder. (a) DTA-TG curves; (b) XRD patterns of calcined powders.

densification of glassy matrix, the glass-ceramic sintered at 1125 °C showed large pores, indicating the over-sintering microstructure. Thus, the sintering process should be attributed to the liquid phase sintering, and the optimal temperature was 1075 °C. Fig. 7 shows the XRD patterns of sintered glass-ceramics. The glassceramic sintered at 1060 °C consisted of quartz, anorthite and hematite phases. With the increase of sintering temperature, the crystallinity was gradually decreased, corresponding to 75% (1060 °C), 61% (1075 °C) and 32% (1125 °C). The quartz phase disappeared at 1125 °C due to the complete dissolution in the glass melt [34]. Hence, the increasing flexural strength below 1075 °C resulted from the improved densification, and the decreasing flexural strength above 1075 °C was associated with the decreased densification and reduced crystallinity [35]. 3.4. Effect of boehmite content on the densification and flexural strength of glass-ceramics Fig. 8 shows the dependence of bulk density and flexural strength on the boehmite content. The bulk density was almost constant below 2 wt % boehmite. After that, it firstly increased and then decreased above 3.5 wt% boehmite, with the maximum density of 2.56 g/cm3. Meanwhile, the flexural strength firstly increased and then decreased above 3 wt% boehmite, indicating that the flexural strength was substantially irrelevant to the bulk density below 2 wt% boehmite. The maximum strength of 125 MPa was far superior to that of natural granite (30 MPa). Fig. 9 shows the SEM images of glass-ceramics with different boehmite contents. Without the boehmite addition, the surface morphology of glass-ceramic showed the porous microstructure with large pores and micropores. As the boehmite content was increased to 3.5 wt %, micropores were completely removed, and the size of large pores simultaneously reduced. Considering the variation of bulk density in Fig. 8, the densification process was controlled by the elimination of large pores. Nonetheless, the densification of glassy matrix did not proceed above 3.5 wt% boehmite. Namely, the excessive boehmite hindered the densification of glass-ceramics. Fig. 10 shows the XRD patterns of sintered glass-ceramics. The crystallinity greatly increased with increasing the boehmite content below 3 wt% boehmite, and slightly increased to 63% at 5 wt% boehmite. The relative proportion of different crystal phases seemed to be constant, implying that the crystal precipitation in the glass matrix was facilitated by the active alumina [36]. With the boehmite increasing, the glassy phase was continuously consumed, and in turn the crystallinity was increased especially below 3 wt% boehmite. The structural evolution demonstrated that the densification of glass-ceramics could be supposed to a three-stage process. In the first stage, the active alumina from boehmite particles reacted with the glassy phase [37]. As a result, the precipitation of anorthite and quartz phases enabled the micropore closure, which was substantially ineffective for large pores. In the second stage, when the boehmite was above 2 wt%, the precipitated crystallites played the role in filling large

Fig. 4. Effect of sintering additives on the bulk density and flexural strength of sintered glass-ceramics.

Fig. 5. Relationship of the bulk density and flexural strength of glass-ceramics with sintering temperature.

boehmite was sintered at different temperatures for 2 h. Fig. 5 shows the bulk density and flexural strength of glass-ceramics. The bulk density and flexural strength firstly increased and then decreased with increasing the sintering temperature. The similar relationship suggests that the flexural strength was substantially influenced by the densification/porosity of glass-ceramics. The maximum bulk density (2.49 g/ cm3) and flexural strength (125 MPa) were achieved at 1075 °C. Fig. 6 shows the SEM images of glass-ceramics. Being sintered at 1060 °C, the glass-ceramic showed the porous under-sintering microstructure, and was nearly densified at 1075 °C. In spite of the complete

4


J. Lu et al.

Fig. 6. SEM images of sintered glass-ceramics with different sintering temperatures. (a) 1060 °C; (b) 1075 °C; (c) 1125 °C.

influenced by the densification and crystallinity. The phase distribution was examined with the backscattered electron imaging. Fig. 11(a) shows the FESEM images of glass-ceramic with 3 wt% boehmite. The white particles represent the crystal phases, and the grey matrix is the glassy phase. The crystallites included coarse particles, fiber bundles and ultrafine particles. The EDS analysis of selected spots were performed to identify the crystal phases, as shown in Table 2. The elemental composition of glassy matrix was similar to that of microcline phase, the source of glassy phase in the sintering process. Compared with granite powder, the glassy matrix (spot 1) was deficient in the magnesium and titanium elements, which were segregated in the crystal phases (spots 5–7). The coarse crystallites (spots 2–4) were enriched in the iron element, and could be assigned to the hematite phase. Also, traces of silicon and aluminum elements were found because of the surrounding glassy matrix. The crystal habits of twin (spot 5) and fiber bundle (spot 6) were typical of the anorthite crystallites [39]. However, the atomic ratio of Si/Al was close to that of albite phase. Judging by the solid solutions of plagioclase, the anorthite phase coexisted with a high proportion of albite phase. The substitution of Ca2+ with Mg2+ in the anorthite phase was energetically favorable due to the smaller ionic radius and higher mobility of Mg2+ ions [40]. The inclusion of iron and titanium ions provided the active sites for the nucleation and crystallization of anorthite phase [41,42]. Ultrafine particles (spot 7) were loosely agglomerated, and contained the main component of silica. Similar to that of glassy matrix, these submicron-sized particles were assigned to the quartz phase. The substitution of Al3+ ions in the Si-O networks was rational because of the similar ionic radii between Al3+ (0.050 nm) and Si4+ (0.042 nm), which was accompanied by the charge balance from the modifying ions of glass networks [43]. Certainly, the mixed glassy matrix among the quartz aggregates also influenced the elemental composition. Fig. 11(b) shows the chemically etched surface of glass-ceramic with an aqueous HF solution (10 wt%). There were numerous fibrous pits and residual tiny particles (inset) on the etched surface. The former was ascribed to the chemically etching of anorthite crystallites, and the latter to the quartz crystallites. In addition to the densification and crystallinity, the extensively distributed anorthite crystallites contributed to the mechanical strengthening of sintered glass-ceramics. In the case of the application in ornamental tiles, the aesthetic appearance of glass-ceramics is necessarily required [44]. As a preliminary experiment, the granite powder with 3 wt% boehmite was added with 1 wt% CaF2 to accelerate the nucleation and crystal growth of glass-ceramics. After sintered at 1100 °C for 2 h and subsequent thermal treatment at 1000 °C for 4 h, a decorative glass-ceramic was achieved. Fig. 12 shows the XRD pattern and digital image of sintered glass-ceramic (inset). The crystal structure consisted of anorthite and augite (CaMg0.85Al0.15Si1.70Al0.30O6, PDF 78–1391). The high proportion of glassy phase (73%) endowed the glossy appearance with white spots. Further works to control the nucleation and crystallization

Fig. 7. XRD patterns of glass-ceramics sintered at different temperatures.

Fig. 8. Dependence of the bulk density and flexural strength on the boehmite content.

pores, and dramatically reduced the pore size. In the third stage, when the boehmite content was above 3.5 wt%, the extensive precipitation of crystal phases dramatically increased the viscosity of glass melt, thereby retarded the densification process [38]. As to the variation of flexural strength, the strengthening below 3 wt % boehmite derived from the increased crystallinity, while the decreasing flexural strength above 3.5 wt% was essentially related to the reduced densification. The disparity in the optimal boehmite contents for the bulk density and flexural strength presumably resulted from the weakening interfaces due to the agglomeration of crystal phases on the grain boundaries. In general, the flexural strength of glass-ceramics was 5


J. Lu et al.

Fig. 9. SEM images of sintered glass-ceramics with different boehmite contents. (a) 0; (b) 2 wt%; (c) 3 wt%; (d) 3.5 wt%; (e) 4%; (f) 5 wt%.

Fig. 10. XRD patterns (a) and crystallinity (b) of glass-ceramics with different boehmite contents.

Fig. 11. FESEM image of glass-ceramics. (a) polished surface; (b) chemically etched surface.

more favorable than the silica and float glass powder for the densification and strengthening of glass-ceramics. With increasing the sintering temperature, the bulk density and flexural strength of glassceramics firstly increased and then decreased, whereas the crystallinity decreased. As the boehmite content was increased, the flexural strength firstly increased and then decreased above 3 wt%, and the crystallinity

process are under way.

4. Conclusions The granite powder was modified and sintered into glass-ceramics with the addition of different sintering additives. The boehmite was 6


J. Lu et al.

Table 2 EDS results of the elemental composition of selected areas (atomic%). Spots

Phases

O

Si

Al

Na

K

1 2 3 4 5 6 7

glass hematite hematite hematite anorthite anorthite quartz

62.6 60.1 55.7 60.0 62.5 62.4 61.4

22.3 1.5 2.2 4.9 14.0 18.0 24.8

8.2 1.4 1.9 2.9 4.6 5.7 5.8

3.1

1.4

1.3 0.8 1.3

0.7 1.4 1.6 2.5

Mg

1.2 5.4 1.3

Ca

Fe

2.0

0.4 37.0 40.2 31.5 7.6 5.8 1.7

0.7 0.8

[10] Ti [11] [12] [13] 6.7 0.3 0.4

[14] [15]

[16] [17]

[18]

[19] [20]

[21]

[22]

[23] [24] [25]

Fig. 12. XRD pattern of the sintered glass-ceramic with 1 wt% CaF2.

[26] [27]

gradually increased to 63% at 5 wt% boehmite. The flexural strength of glass-ceramics depended on the densification and crystallinity. The decorative glass-ceramics with high flexural strength are promising for the practical reutilization of granite wastes in the ornamental tiles.

[28] [29] [30]

Acknowledgements

[31]

This work was financially supported by the China Scholarship Council (Grant No. [2016] 5113) and Postgraduate Innovation and Entrepreneurship Fund of Nanchang Hangkong University (CXCYXY201701). The authors are grateful to Dr. Liping Deng and Dr. Delai Ouyang for the assistance in the mechanical testing of glassceramics.

[32] [33]

[34] [35]

[36]

References [1] Secretariat of China Stone Association, Analysis of economic operation of China stone industry in 2016 and outlook in 2017, Stone (4) (2017) 14–17. [2] R.A. Hamza, S. El-Haggar, S. Khedr, Marble and granite waste: characterization and utilization in concrete bricks, Int. J. Biosci. Biochem. Bioinform 1 (2011) 286–291. [3] L.L. Aguiar, C.B. Tonon, E.T. Nunes, A.C. Braga, M.A. Neves, J.A. de Oliveira David, Mutagenic potential of fine wastes from dimension stone industry, Ecotoxicol. Environ. Saf. 125 (2016) 116–120. [4] C. Furcas, G. Balletto, Increasing the value of dimension stone waste for a more achievable sustainability in the management of non-renewable resources, J. Solid Waste Technol. Manag. 40 (2014) 185–196. [5] G. Medina, I.F. Saez del Bosque, M. Frías, M.I. Sanchez de Rojas, C. Medina, Granite quarry waste as a future eco-efficient supplementary cementitious material (SCM): scientific and technical considerations, J. Clean. Prod. 148 (2017) 467–476. [6] A. Rana, P. Kalla, H.K. Verma, J.K. Mohnota, Recycling of dimensional stone waste in concrete: a review, J. Clean. Prod. 135 (2016) 312–331. [7] P. Torres, H.R. Fernandes, S. Olhero, J.M.F. Ferreira, Incorporation of wastes from granite rock cutting and polishing industries to produce roof tiles, J. Eur. Ceram. Soc. 29 (2009) 23–30. [8] F.G. Diasa, A.M. Segadãesb, C.A. Perottonia, R.C.D. Cruz, Assessment of the fluxing potential of igneous rocks in the traditional ceramics industry, Ceram. Int. 43 (2017) 16149–16158. [9] P.G. Attrill, F.G.F. Gibb, Partial melting and recrystallization of granite and their

[37]

[38] [39] [40]

[41]

[42]

[43] [44]

7

application to deep disposal of radioactive waste part 1-rationale and partial melting, Lithos 67 (2003) 103–117. M.T.B. Silva, B.S. Hermo, E. Garcia-Rodeja, N.V. Freire, Reutilization of granite powder as an amendment and fertilizer for acid soils, Chemosphere 61 (2005) 993–1002. E. Wolff, W.K. Schwabe, S.V. Conceiçao, Utilization of water treatment plant sludge in structural ceramics, J. Clean. Prod. 96 (2015) 282–289. M. Romeroa, J.M. Rincona, A. Acosta, Effect of iron oxide content on the crystallisation of a diopside glass-ceramic glaze, J. Eur. Ceram. Soc. 22 (2002) 883–890. R.C. Silva, S.A. Pianaro, S.M. Tebcherani, Preparation and characterization of glazes from combinations of different industrial wastes, Ceram. Int. 38 (2012) 2725–2731. G.A. Khater, Diopside-anorthite-wollastonite glass-ceramics based on waste from granite quarries, Glass Technol. Eur. J. Glass Sci. Technol. A 51 (2010) 6–12. J.F. Kang, J. Wang, J.S. Cheng, J. Yuan, Y.S. Hou, S.Y. Qian, Crystallization behavior and properties of CaO-MgO-Al2O3-SiO2 glass-ceramics synthesized from granite wastes, J. Non-Cryst. Solids 457 (2017) 111–115. W.Y. Zhang, H. Gao, Y. Xu, Sintering and reactive crystal growth of diopside-albite glass-ceramics from waste glass, J. Eur. Ceram. Soc. 31 (2011) 1669–1675. P.J. Tian, J.S. Cheng, G.K. Zhang, Z.X. Chen, Q. Wang, Crystallization and luminescence properties of Eu2+ doped diopside glass ceramics, Glass Phys. Chem. 36 (2010) 431–435. R.L. Leonard, S.K. Gray, C.J. Alvarez, A.K. Moses, L.F. Arrowood, A.R. Lubinsky, A.K. Petford-Long, J.A. Johnson, Evaluation of a fluorochlorozirconate glassceramic storage phosphor plate for gamma-ray computed radiography, J. Am. Ceram. Soc. 98 (2015) 2541–2547. M.A. Carpenter, J.D.C. Mcconnell, Enthalpies of ordering in the plagioclase feldspar solid solution, Geochem. Cosmochim. Acta 49 (1985) 947–966. J.G. He, B. Ma, M.L. Kang, C.L. Wang, Z. Nie, C.L. Liu, Migration of 75Se(IV) in crushed Beishan granite: effects of the iron content, J. Hazard Mater. 324 (2017) 564–572. D.K. Bayel, Z. Karaca, V. Onen, A.H. Deliormanli, The relationship between mineral content and flocculant characteristics for slurry waste water recycling at marble processing plants, Mine Water Environ. 35 (2016) 332–336. P. Hartlieb, M. Toifl, F. Kuchar, R. Meisels, T. Antretter, Thermo-physical properties of selected hard rocks and their relation to microwave-assisted comminution, Miner. Eng. 91 (2016) 34–41. M. Hojamberdiev, A. Eminov, Y.H. Xu, Utilization of muscovite granite waste in the manufacture of ceramic tiles, Ceram. Int. 37 (2011) 871–876. R.J. Saikkonen, I.A. Rautiainen, Determination of ferrous iron in rock and mineral samples by three volumetric methods, Bull. Geol. Soc. Finland 65 (1993) 59–63. M.R. Rovetta, J.D. Blacic, R.L. Hervig, J.R. Holloway, An experimental study of hydroxyl in quartz using infrared spectroscopy and ion microprobe techniques, J. Geophys. Res. 94 (1989) 5840–5850. Y.S. Fang, L.X. Hu, The important mineral ingredients of ceramics: feldspars, Bull. Chin. Ceram. Soc. 1 (1980) 67–73. R. Sturm, Microscopy and microanalysis of magmatic and metamorphic minerals part 2: feldspar, Microsc. Today 18 (2010) 18–24. C.J. Brinker, Hydrolysis and condensation of silicates: effects on structure, J. NonCryst. Solids 100 (1988) 31–50. S. Natansohn, A.E. Pasto, W.J. Rourke, Effect of powder surface modifications on the properties of silicon nitride ceramics, J. Am. Ceram. Soc. 76 (1993) 2273–2284. P. Hrma, J. Marcial, Dissolution retardation of solid silica during glass-batch melting, J. Non-Cryst. Solids 357 (2011) 2954–2959. C.Y. Wang, Y. Tao, Glass Properties and Process Manual, Chemical Industry Press, Beijing, 2014. E. Plevova, L. Vaculikova, A. Kozusnikova, M. Ritz, G.S. Martynkova, Thermal expansion behavior of granites, J. Therm. Anal. Calorim. 123 (2016) 1555–1561. S.M. Kim, Y.J. Lee, J.W. Bae, H.S. Potdar, K.W. Jun, Synthesis and characterization of a highly active alumina catalyst for methanol dehydration to dimethyl ether, Appl. Catal. A 348 (2008) 113–120. K. Devineau, M. Pichavant, F. Villieras, Melting kinetics of granitic powder aggregates at 1175°C, 1 atm, Eur. J. Mineral 17 (2005) 387–398. J.S. Lu, X.Q. Cong, Z.Y. Lu, Influence of magnesia on sinter-crystallization, phase composition and flexural strength of sintered glass-ceramics from waste materials, Mater. Chem. Phys. 174 (2016) 143–149. L. Cormier, O. Dargaud, N. Menguy, G.S. Henderson, M. Guignard, N. Trcera, B. Watts, Investigation of the role of nucleating agents in MgO-SiO2-Al2O3-SiO2TiO2 glasses and glass-ceramics: a XANES Study at the Ti K- and L2,3-edges, Cryst. Growth Des. 11 (2011) 311–319. W.W. Xuan, Q. Wang, J.S. Zhang, D.H. Xia, Influence of silica and alumina (SiO2 + Al2O3) on crystallization characteristics of synthetic coal slags, Fuel 189 (2017) 39–45. S. Samal, S. Kim, H. Kim, Effects of filler size and distribution on viscous behavior of glass composites, J. Am. Ceram. Soc. 95 (2012) 1595–1603. H.F. Xu, P.R. Buseck, Twinning in synthetic anorthite: a transmission electron microscopy investigation, Am. Mineral. 82 (1997) 125–130. G.Y. Yang, H. Yang, X.Z. Guo, W.Y. Li, Effect of mass ratio of CaO/MgO on crystallization of CaO-MgO-Al2O3-SiO2 glass-ceramics, J. Chin. Ceram. Soc. 38 (2010) 2045–2049. Z. Khalkhali, Z. Hamnabard, B.E. Yekta, M. Nasiri, E. Khatibi, Sintering behavior and machinability of phlogopite glass-ceramics containing Fe2O3, J. Mater. Eng. Perform. 22 (2013) 528–535. S. Taruta, K. Watanabe, K. Kitajima, N. Takusagawa, Effect of titania addition on crystallization process and some properties of calcium mica-apatite glass-ceramics, J. Non-Cryst. Solids 321 (2003) 96–102. U. Seifert-Kraus, H. Schneider, Cation distribution between cristobalite, tridymite, and coexisting glass phase in used silica bricks, Ceram. Int. 10 (1994) 135–142. I. Ponsota, E. Bernardo, E. Bontempi, L. Depero, R. Detsch, R.K. Chinnam, A.R. Boccaccini, Recycling of pre-stabilized municipal waste incinerator fly ash and soda-lime glass into sintered glass-ceramics, J. Clean. Prod. 89 (2015) 224–230.