1 Introduction
Industrial sludge (IS), as a solid waste, contains a great deal of toxic inorganic and organic pollutants [1], which can pose a serious threat to human health and the environment when it is treated by landfilling or stacking. Therefore, the reasonable reuse of IS has attracted an increasing amount of attention. IS has a high volatile content and a low fixed carbon content. Therefore, IS is similar to biomass because it is not only a solid waste, but also an energy material [2,3]. The mixed heat treatment of solid waste and coal is an efficient approach (e.g., combustion, pyrolysis, and gasification) [4,5]. However, with the increasingly higher requirements of the government for environmental protection, the clean and efficient utilization of coal resources is constantly putting forward higher requirements. The co-gasification of solid waste and coal is a promising method, which cannot only improve the slag-tapping performance of coal ash, but also reduce the damage to the environment [6]. Previous studies also prove that the co-gasification of IS and coal is an effective approach to achieve harmless and sustainable treatment of IS [7,8].
In the co-gasification process, organic matters are gasified into syngas, and inorganic minerals are transformed into liquid molten slag at high temperature, flowing out along the wall and entering the slag bath [9]. Generally, continuous and stable slag-tapping is a prerequisite for the normal operation of the gasifier [10]. The ash fusion temperatures (AFTs) and viscosity-temperature characteristics are the key parameters guiding the stable operation of the gasifier [11,12]. AFTs are the primary basis for coal blending and optimization of operating parameters [13–15]. The operating temperature of the gasifier is usually 50−200°C higher than the flow temperature (FT) to ensure complete melting and smooth discharge of minerals [16]. As another important parameter, the viscosity is usually required to be 2.5 − 25 Pa·s [17–19]. When the viscosity is below 2.5 Pa·s, the excessively flowing liquid slag can continually scour and erode the refractory brick wall; when the viscosity is above 25 Pa·s, the slag is difficult to be discharged, which can cause blockage of the slag outlet [20,21].
At present, the research on the co-gasification of IS and coal was principally focused on the ash melting behavior [22,23]. For example, Schwitalla et al. [24] investigated the slagging characteristics of lignite and its mixture with sludge. It was demonstrated that when the content of sludge ash was increased to 50% (mass percentage), FT could be significantly reduced. At the same time, it was found that the FactSage thermodynamic calculations were very consistent with the experimental ash melting behavior. Similarly, Folgueras et al. [25] studied the slagging behavior of three types of sludge on lignite and found that the addition of sludge could reduce the AFTs. Meanwhile, based on the ternary phase diagram of SiO2-Al2O3-CaO, it was illustrated that most of the minerals in the mixed ash were located in the low temperature region and close to eutectics. In addition, Li et al. [26] researched the effects of industrial sludge on AFTs of three kinds of high-melting-point coal. It was considered that the addition of iron-bearing industrial sludge reacted with mullite in high-melting-point coal ash, and eventually transformed into low-melting-point hercynite. However, in some cases, the assessment method of AFTs was feasible [27,28]. However, in actual industrial gasification operation, for some coal, although the FT was lower than the operating temperature of the gasifier, the fluidity of molten slag was still very poor [29]. Therefore, to achieve the optimal slag-tapping conditions, it was quite necessary to consider the viscosity-temperature characteristic parameters during the co-gasification process [30]. However, up to the present, the research on co-gasification of industrial sludge and coal has mainly been focused on the ash melting characteristics, while little research has been conducted on the crystallization and viscosity-temperature characteristics. Since the ash melting characteristics and viscosity-temperature characteristics jointly guide the stable operation of gasifier, it is particularly important to study the viscosity-temperature characteristics in the process of co-gasification of IS and coal.
The co-gasification of IS and coal is an effective way to realize the harmless and sustainable utilization of industrial solid waste. During the co-gasification, the fluidity of molten slag is determined by both the melting and viscosity-temperature characteristics of the coal ash. However, the research on co-gasification of IS and coal are mainly focused on the ash melting characteristics, and few studies on the crystallization and viscosity-temperature characteristics are conducted. Therefore, the effect of industrial sludge addition on the crystallization and viscosity-temperature characteristics of Ningdong coal was studied in this work. XRD and FTIR were employed to characterize the mineral phase and slag structure. In addition, the crystal morphology was in situ observed by the HTSOM. Moreover, SEM-EDS was adopted for high resolution and element distribution characterization. Furthermore, the viscosity was calculated using the Einstein-Roscoe empirical formula and FactSage thermodynamic software. Collectively, the purpose of this study is to provide some insights for the resource treatment of industrial sludge, hoping to provide some theoretical support for the slag flow mechanism in the process of co-gasification of industrial sludge and coal to reduce the frequency of accidental shutdown of the gasifier.
2 Materials and methods
2.1 Materials
In this work, the Shuangmazao coal (SMZ) and industrial sludge (IS) provided by CHN Energy Ningxia Coal Industry Co., Ltd., were selected as raw materials. According to GB/T212-2008 and GB/T476-2001, proximate and ultimate analyses of these two raw materials were conducted, as listed in Tab.1 and Tab.2. Ash samples were prepared in a muffle furnace at 815°C as per GB/T 1574-2007. The ash chemical compositions were determined by X-ray fluorescence spectrometer (PANalytical Axios; RIGAKU ZSX Priums), and the results were presented in Tab.3 where it could be seen that the SiO2 and Al2O3 contents were higher in SMZ, while the CaO and Fe2O3 contents were higher in IS.
Tab.1 Proximate analysis of SMZ and IS |
| Sample | Proximate analysis (d)/% (mass percentage) | ||
|---|---|---|---|
| VM | FC | A | |
| SMZ | 27.14 | 54.52 | 18.34 |
| IS | 41.71 | 20.46 | 37.83 |
Notes: VM—volatile matter; FC—fixed carbon; d—dry basis. |
Tab.2 Ultimate analysis of SMZ and IS |
| Sample | Ultimate analysis (d)/% (mass percentage) | ||||||
|---|---|---|---|---|---|---|---|
| A | C | H | N | S | O* | ||
| SMZ | 18.34 | 63.01 | 4.10 | 0.74 | 1.86 | 11.95 | |
| IS | 37.83 | 14.28 | 7.91 | 1.80 | 1.72 | 36.46 | |
Notes: d—dry basis; *— calculated by difference. |
Tab.3 Ash chemical compositions of SMZ and IS |
| Sample | Compositions/% (mass percentage) | |||||||||
|---|---|---|---|---|---|---|---|---|---|---|
| SiO2 | Al2O3 | Fe2O3 | CaO | Na2O | K2O | MgO | SO3 | Others | B/A | |
| SMZ | 50.84 | 21.05 | 6.70 | 8.90 | 1.95 | 1.67 | 3.54 | 2.61 | 2.74 | 0.32 |
| IS | 33.12 | 13.82 | 12.51 | 21.08 | 6.17 | 1.05 | 4.94 | 4.89 | 2.42 | 0.97 |
According to the GB/T219-2008 standard, the SDAF4000 automatic analyzer was applied to determine the ash fusion temperatures (AFTs) in a weakly reducing atmosphere (CO:CO2 = 3:2, volumetric) and the results were tabulated in Tab.4 where almost no significant difference could be observed in AFTs between SMZ and IS.
Tab.4 Ash fusion temperatures of SMZ and IS |
| Sample | Ash fusion temperatures/°C | ||||
|---|---|---|---|---|---|
| DT | ST | HT | FT | ||
| SMZ | 1190 | 1214 | 1219 | 1230 | |
| IS | 1182 | 1220 | 1223 | 1228 | |
Notes: DT— deformation temperature; ST— softening temperature; HT— hemispherical temperature; FT—flow temperature. |
2.2 Ash samples preparation
IS was added to the SMZ coal with mass fractions of 0, 20%, 40%, 60%, and 80% to prepare mixed samples, which were named IS0, IS2, IS4, IS6, and IS8, respectively (dimensionless parameter). Subsequently, the ash samples were prepared according to GB/T 1574-2007. First, the mixed sample was heated to 500°C within 30 min and kept for 30 min. Then, they were heated to 815°C and maintained for 2 h to ensure that the organic matter was fully oxidized.
2.3 Experimental methods
2.3.1 In situ crystallization observation using the HTSOM
A HTSOM (LINKAM TIS0500, England) was employed to in situ observe the crystal morphology variations during the cooling process. The temperature control procedure is exhibited in Fig.1. The HTSOM equipment and the specific operation process had been introduced in detail [14,19]. Moreover, each experiment was repeated at least three times for data accuracy.
2.3.2 XRD analysis
The ash samples were heated from room temperature to the target temperature and kept for 30 min to fully react in a weak reducing atmosphere. After that, the molten slag was quickly extracted and quenched in liquid nitrogen. Then, the quenched slag was grounded and sieved to less than 200 μm for XRD analysis. The quenched slag samples were characterized by Bruker-AXS X-ray diffraction (XRD) with Cu Kα radiation (40 kV, 40 mA). The powder sample was placed on the sample stage and scanned in a step size of 0.02° within a 2θ range of 5° − 80°.
2.3.3 Thermodynamic calculation
The FactSage software package has been widely adopted to predict the ash fusion temperature and the slag viscosity [33]. In this work, using the FToxid and FactPS database, the main components of the ash samples (SiO2, Al2O3, Fe2O3, CaO, Na2O, and MgO) were selected in the Equilib module to calculate the minerals transformation behavior. The calculated temperature ranged from 1300 to 1600°C in steps of 50°C. By analyzing the minerals evolution, the contents of liquid phase and solid phase could be determined.
The Einstein-Roscoe empirical formula (Eq. (1)) was proverbially used in the calculation of the slag viscosity of solid-liquid mixed phase [34,35]. The liquid phase temperature (Tliq: the temperature at which the solid phase disappeared) was determined by the minerals evolution calculated by the Equilib module. Therefore, the calculation of the viscosity was divided into two cases: (1) When the temperature was higher than Tliq, the slag was pure liquid phase. At this time, the liquid phase composition and content calculated by Equilib were directly input into the viscosity module to calculate the viscosity of the sample higher than Tliq; (2) when the temperature was lower than Tliq, the slag was a solid-liquid mixed phase. Similarly, the Equilib module calculation results were used to determine the solid phase content and liquid phase composition and content in the molten slag, and then the corresponding liquid phase composition and content were input into the viscosity module to calculate the liquid phase viscosity. Finally, according to the solid content and liquid viscosity, the viscosity of the sample lower than Tliq was calculated by the Einstein-Roscoe empirical formula.
2.3.4 Characterization of slag structure
The structure of quenched slag was characterized by using a Fourier transform infrared spectrometer (spectrum II, PerkinElmer, USA). The KBr drifts technique was used in the experiment. The powder sample was accurately mixed with KBr in a mass ratio of 1:200. The mixture was adequately grounded and then pressed into a thin tablet at 15 MPa. The spectral recording ranged from 400 to 4000 cm−1, and the resolution was 0.4 cm−1 [36].
2.3.5 SEM-EDS analysis
The microstructure and elemental composition of the sputtered Au-Pd coating slag after the HTSOM test was determined by using a scanning electron microscopy (Talos-F200S) coupled with an energy dispersive X-ray spectrometry (EDS) at an accelerating voltage of 10 kV. The elemental composition analysis was the result of point scanning on the crystal surface.
2.3.6 Viscosity measurement
The viscosity was measured by using a RV DVIII high temperature rotational viscometer in a mild reducing atmosphere (CO2:CO = 2:3, volumetric). First, the pre-melted slag required to be prepared, which could be obtained by heating about 100 g ashes to 150°C higher than Tliq and maintaining it for 30 min to achieve equilibrium. After that, about 50 g pre-melted slags were crushed to 2 mm for viscosity testing. The apparatus was increasingly heated to 900°C at 15°C/min, then heated to 50°C higher than Tliq at 5°C/min, and the temperature was maintained for 30 min to obtain fully molten slag. Afterwards, the spindle was tardily immersed in the molten slag to start measuring the viscosity, and the cooling rate was 2°C/min. When the upper limit was exceeded, the viscometer stopped measuring.
3 Results and discussion
3.1 High-temperature crystallization
3.1.1 In situ crystallization morphology
The crystal morphological variations of different samples observed by the HTSOM are shown in Fig.2 while a photograph taken with a projection light source when the sample is cooled to room temperature is displayed in Fig.3, of which, Fig.2(a) manifests the morphology change of IS4. It can be seen that IS4 shows a homogeneous melt and does not precipitate crystals during the cooling process, nor do IS0 and IS2 in the cooling process. Therefore, the crystal morphology of IS0 and IS2 is not exhibited. Meanwhile, it can be distinctly observed from Fig.3(a) that when the molten slag is cooled to room temperature, the surface of the molten slag is in a uniform glass state. In this case, the crystallization may be completely inhibited due to the high glass-forming ability (GFA) of the IS0, IS2, and IS4 slag. This slag characteristic is usually related to the minimum cooling rate at which the glass phase is formed. Fig.2(b) shows the crystal morphology change of IS6 during the cooling process. The fine needle-shaped crystals are formed at 1400°C. With the decrease of temperature, needle-shaped crystals continue to grow, and the aspect ratio of needle-shaped crystals increase. Finally, the growth of crystal stops at 1300°C. The crystal morphology at room temperature is shown in Fig.3(b), and the majority of fine needle-shaped crystals can be observed more clearly. Fig.2(c) shows the crystal morphology change of IS8 during the cooling process. It can be seen that rod-shaped crystals are precipitated first. As the temperature decreases, a large number of rod-shaped crystals are continuously precipitated, and the aspect ratio of rod-shaped crystals is also increased. Finally, the volume fraction and aspect ratio of the crystal do not change at about 1300°C. Meanwhile, the crystal morphology of IS8 at room temperature is exhibited in Fig.3(c), and the majority of rod-shaped crystals can be observed. However, compared with the fine needle-shaped crystals precipitated by IS6, the aspect ratio of the crystals precipitated in the IS8 is much greater than that of IS6 during the cooling process. This indicates that IS8 has a high crystallization rate. Crystallization usually involves two stages, namely nucleation and crystal growth. The nucleation rate and the crystal growth rate affect the crystallization rate development, thereby affecting the change of the viscosity. The crystallization behavior of slag also affects crystallization kinetics. In the classical nucleation theory, the chemical potentials and interface energy of the solid-liquid phase determine the nucleation rate of the solid-phase nuclei precipitated.
3.1.2 Surface morphology characterization via SEM
To more intuitively observe the effect of IS additive on the crystal morphology of the SMZ coal, SEM was used to perform high-resolution characterization of the samples after the HTSOM experiment, and the results were shown in Fig.4(a)−4(c). At the same time, the surface elements were investigated with an energy spectrometer (Fig.4(d)). It can be seen from Fig.4(a) that the slag of IS4 is a homogeneous melt without crystal precipitation. The reason for this is that when the addition proportion of IS is low (IS0−IS4), the content of CaO in the ash is low while SiO2 and Al2O3 are high, which makes the slag have a high glass forming ability (GFA), thus inhibiting the formation of crystals and existing in the form of glass. It is observed from Fig.4(b) that there are a large number of fine needle-shaped crystals on the molten slag surface. Fig.4(c) is the morphology of the SEM image of IS8 crystal. It can be seen that the molten slag appears to be in the form of rod-shaped crystals. The element distribution results of crystals in IS6 and IS8 are shown in Fig.4(d). The main elements that form crystals are Si, Al, Ca, and O, with Fe and Mg rarely involved. The ratio of Si:Al:Ca is about 2:2:1, which is the same as the chemical composition of anorthite. The reason for this is that, with the addition of IS, the content of CaO in blended ash increases. The increased CaO content could react with SiO2 and Al2O3 in the ash, causing the slag to precipitate anorthite crystals driven by the temperature difference (2SiO2 + Al2O3 + CaO→CaAl2Si2O8). However, compared to IS6 (needle-like), the IS8 (rod-shaped) crystals have a larger aspect ratio, which indicates that the crystal growth of IS8 is more sufficient during the cooling process.
3.2 Mineral analyses
3.2.1 Raw ash mineral analysis
The mineral components of the SMZ coal ash and the IS ash prepared at 815°C are shown in Fig.5 where it can be seen that the mineral components of the SMZ coal ash are quartz (SiO2), hematite (Fe2O3), and anhydrite (CaSO4), among which quartz has the strongest diffraction peak. In addition, since the diffraction intensity of minerals is proportional to its content [36], the main mineral in the SMZ coal ash is quartz. The mineral components of the IS ash are quartz (SiO2), hematite (Fe2O3), anhydrite (CaSO4), and lime (CaO). Compared with the SMZ coal ash, the content of the quartz of the IS ash is significantly reduced while that of hematite and anhydrite is increased, and a new mineral lime (CaO) has appeared. Therefore, the IS ash is rich in calcium and iron.
3.2.2 Influence of IS addition on mineral evolution
Fig.6 shows the XRD patterns of samples with different IS proportions quenched at 1350°C. It can be seen that for IS0, IS2, and IS4, the quenched slag exists in an amorphous form. For IS6 and IS8, many strong diffraction peaks are observed in the XRD patterns. After matching, these substances are identified as anorthite, which also indicates that anorthite is the main component in the large number of fine needle-shaped crystals and rod-shaped crystals observed by the HTSOM. Moreover, IS8 exhibites more and stronger anorthite diffraction peaks than IS6. It was reported that the diffraction intensity was proportional to the content for the same substance [37]. In other words, the content of anorthite precipitated in IS8 is higher than that in IS6 during the cooling process. This is consistent with the in situ observation results of the HTSOM. The volume fraction and aspect ratio of IS8 crystals precipitated in the cooling process are much larger than those of IS6.
3.3 Influence of IS addition on molten slag structure
FTIR spectra were adopted to characterize the microstructure information of different slag samples. The FTIR results and typical deconvolution of the FTIR spectra are shown in Fig.7 and Fig.8. It was accepted that the FTIR spectra of silicate slag were focused in the wavenumber region between 800 and 1200 cm−1, which was related to the symmetric stretching vibration of [SiO4] tetrahedron [38]. The characteristic stretching vibration of the SiO4 tetrahedron was distinguished by introducing the Qn unit, where the index n was the amount of Si-O-Si bridging oxygen and represented the molten slag polymerization degree. The index “n” was defined as a different microstructure from 0 to 4. For example, Q0 existed as a monomer such as [SiO4]4− (related to 850 − 880 cm−1), Q1 was indicated as a dimer structure like [Si2O7]6− (related to 900 − 920 cm−1), Q2 represented a chain structure such as [SiO3]2− (related to 950 − 1000 cm−1), Q3 was a planar layered structure like [Si2O5]2− (related to 1050 − 1100 cm−1), and Q4 was the three-dimensional network structure like SiO2 (related to 1060 − 1200 cm−1) [39]. Therefore, the higher n value represents a higher polymerization degree of silicate slag and a stronger aluminosilicate skeleton. As presented in Fig.7, from IS0 to IS8, the peak shifts to a low wave number, which indicates that the addition of IS can reduce the molten slag polymerization degree.
Fig.9 exhibites the quantitative results of Qn units of different slag samples. As can be observed from Fig.9, with the increase of IS proportion, the contents of Q0, Q1, and Q2 increase in varying degrees. On the contrary, the contents of Q3 and Q4 decrease to different degrees, and the reduction of Q3 is the most significant. Therefore, the variation of the Qn unit content suggests that the polymerization degree of high temperature slag decreases continuously with the increase of the IS content. This is due to the relatively high content of SiO2 and Al2O3 for SMZ. According to the network structure theory, SiO2 and Al2O3 components can form a tetrahedron and become the basic units in the silicate network structure at a high temperature. With the increase of the SiO2 and Al2O3 content, the network structure becomes more complex and polymerized. However, IS had a higher content of alkaline oxides, and Fe2+ and Ca2+ could be connected with the unsaturated O2− in the silicate network structure to destroy the network structure [40,41]. Moreover, with the increase of the alkaline oxide content, more unsaturated O2− can be obtained from the silicate network structure, which destroys the network structure complexity and makes the network structure smaller.
Here, the difference of in situ crystallization morphology of different samples could be well explained by the variation of molten slag polymerization degree. For IS0, IS2, and IS4, the molten slag polymerization degree is high and leads to a weak interionic migration, which was ultimately not conducive to the formation of crystal nucleus and crystal growth. However, for IS6 and IS8, fine needle-shaped and rod-shaped crystals are precipitated during the cooling process. The reason for this is that the molten slag polymerization degree decreases continuously with the increase of IS proportion. As a result, the migration ability between ions is enhanced driven by the temperature difference, which contributes to the formation of crystal nucleus and the growth of crystal. In addition, since the polymerization degree of IS8 is lower than that of IS6, the volume fraction and aspect ratio of IS8 are much larger than those of IS6. Therefore, the evolution of microstructure can be well related to the variation of crystal morphology.
3.4 Viscosity-temperature curves
Kondratiev and Ilyushechkin [42] and Ge et al. [43] investigated the effect of solid volume fraction and morphology in molten slag on viscosity, and explained that crystal morphology (e.g., the size and shape) had a great effect on viscosity. Therefore, to better expound the influence of molten slag microstructure on the viscosity-temperature characteristics, the viscosity of different samples at 1300 − 1600°C was calculated by FactSage software in combination with the Einstein-Roscoe empirical formula, as shown in Fig.10(a). Meanwhile, a group of sample was selected to compare the viscosity measured by the experiment and the viscosity calculated by the simulation (e.g., IS4). It can be seen from Fig.10(b) that there is still a certain deviation between the simulated viscosity and the actual viscosity. This may be caused by the fact that the calculation method of FactSage simulation software is the global equilibrium analysis [42,44]. However, under actual operating conditions, the overall state of the gasifier may deviate far away from the theoretical global equilibrium. Therefore, there is some deviation between the actual viscosity and the simulated viscosity. Nevertheless, the viscosity calculated by FactSage simulation is still instructive.
In the simulation, Fe2+/Fe3+ = 8:2 (mass ratio) was set to eliminate the influence of atmosphere on the Fe valence state [38]. Moreover, it can be seen from Tab.3 that the S/A of SMZ coal is so close to that of IS that the effect of S/A on crystallization and viscosity could be eliminated [45]. It can be seen from the results that the viscosity increases with the decrease of temperature. With the increase of IS proportion, the viscosity rise rate declines constantly. Therefore, the addition of IS can significantly reduce the slag viscosity. In combination with the influence of IS addition on crystal morphology, molten slag structure and viscosity, it can be seen that the slag with a high polymerization degree exhibits a higher viscosity, which limits the ion migration ability in the liquid molten slag and ultimately makes the slag difficult to crystallize. Conversely, the slag with low polymerization degrees exhibits a lower viscosity, which enhances the ion migration ability in the slag, and eventually contributes to the formation of crystal nucleus and the growth of crystal.
Generally, to guarantee the normal slag-tapping of the gasifier, the viscosity at the operating temperature required is between 2.5 and 25 Pa·s (shaded in Fig.10(a)) [17]. In addition, it was reported that the operating temperature of the gasifier should be about 150 − 200°C higher than the FT of coal ash [38]. Therefore, according to Tab.4, the operating temperature of the gasifier should reach at least about 1400°C to insure normal liquid slag-tapping [46,47]. For IS0, IS2, and IS4, the excessive viscosity at the operating temperature will lead to blockage of the slag-tapping outlet; otherwise, a higher temperature was required to ensure normal slag-tapping, which will significantly increase energy consumption. However, for IS8, too low a viscosity could make the fluidity of liquid slag too strong, which could accelerate the erosion and the fall off of refractory bricks [19,48]. The above analysis indicates that IS6 is more suitable. Therefore, the co-gasification of IS with appropriate proportion and coal was an effective method, which could not only realize the resource utilization of solid waste, but also ensure a lower operating temperature and avoid the slag-tapping problems.
4 Conclusions
The effects of IS addition on the crystallization and viscosity of Shuangmazao (SMZ) coal were investigated by means of HTSOM, a SEM-EDS, XRD, a FTIR, and FactSage software. Based on the experiment, it can be concluded that due to the high content of SiO2 and Al2O3 in the SMZ coal ash, the slag with a complex network structure is formed at high temperatures, which leads to the weakening of the migration ability between ions. The SMZ coal ash does not precipitate any crystals during cooling.
IS6 and IS8 precipitate fine needle-shaped crystals and rod-shaped crystals respectively during the cooling process, which are matched to anorthite. The reason for this is that the addition of IS with the high basic oxides (CaO and Fe2O3) can connect with the unsaturated O2− in the silicate network structure, which destroys the complex network structure and reduces the polymerization degree of the molten slag. The reduction of the slag polymerization degree enhances the ion mobility, which is beneficial to the formation of crystal nucleus and the growth of crystals.
According to the crystal morphology of IS6 and IS8, because the slag polymerization degree of IS8 is relatively low and the crystals are easy to grow, the aspect ratio of the crystals precipitated by IS8 is larger than that of IS6.
The calculation of viscosity by FactSage thermodynamics software suggests that IS additive could significantly reduce the viscosity to meet the requirements of liquid slag-tapping gasifiers.