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Interfacial Behaviour in Ferroalloys: The Influence of Sulfur in FeMn and SiMn Systems

The present study has investigated the influence of sulfur content in synthetic FeMn and SiMn from 0 to 1.00 wt pct on interfacial properties between these ferroalloys and slags. The effect of experimental parameters such as temperature and holding time was evaluated. Interfacial interaction between ferroalloys and slags was characterized by interfacial tension and apparent contact angle between metal and slag, measured based on the Young–Laplace equation and an inverse modelling approach developed in OpenFOAM. The results show that sulfur has a significant influence on both interfacial tension and apparent contact angle, decreasing both values and promoting the formation of a metal-slag mixture. Despite the fact that sulfur was added only to the ferroalloys, most of sulfur is distributed into slag after reactions with the metal phase. Increasing the maximum experimental temperature in the sessile drop furnace also resulted in a decrease of both interfacial properties, resulting in higher mass transfer rates and intensive reactions between metal and slag. The effect of holding time demonstrated that after reaching equilibrium in FeMn-slag and SiMn-slag systems (both with and without sulfur), interfacial tension and apparent contact angle remain constant.

The present study has investigated the influence of sulfur content in synthetic FeMn and SiMn from 0 to 1.00 wt pct on interfacial properties between these ferroalloys and slags. The effect of experimental parameters such as temperature and holding time was evaluated. Interfacial interaction between ferroalloys and slags was characterized by interfacial tension and apparent contact angle between metal and slag, measured based on the Young-Laplace equation and an inverse modelling approach developed in OpenFOAM. The results show that sulfur has a significant influence on both interfacial tension and apparent contact angle, decreasing both values and promoting the formation of a metal-slag mixture. Despite the fact that sulfur was added only to the ferroalloys, most of sulfur is distributed into slag after reactions with the metal phase. Increasing the maximum experimental temperature in the sessile drop furnace also resulted in a decrease of both interfacial properties, resulting in higher mass transfer rates and intensive reactions between metal and slag. The effect of holding time demonstrated that after reaching equilibrium in FeMn-slag and SiMn-slag systems (both with and without sulfur), interfacial tension and apparent contact angle remain constant.

I. INTRODUCTION
HIGH-CARBON FeMn and SiMn are produced in submerged arc furnaces (SAF) by carbothermic reduction of manganese ores with the addition of carbon materials and fluxes. The main products generated in SAFs in ferroalloy production are molten metal and slag which accumulate during smelting and, therefore, must be removed from the furnace by performing an operation called tapping. During tapping, molten materials flow out through a tap-hole and into ladles, where the first ladle usually serves as a metal reservoir and subsequent ladles are used as slag reservoirs. Since the separation of metal and slag in the metal ladle occurs naturally due to their difference in density, slag tends to accumulate at the top of the metal ladle while metal settles to the bottom. Due to the turbulence of the tapping flow and interfacial interaction of metal and slag, metal droplets are formed in slag, forming a so-called metal-slag emulsion. [1] After the first ladle is completely filled, slag begins to overflow to the slag ladles, entraining a large number of metal droplets. Metal entrained in slag is considered a loss, and this generally reduces the process efficiency, [2,3] mainly for the reason that further post-processing of slag with entrained metal droplets requires additional costs.
Interfacial phenomena are vital for ferroalloy production, as a better understanding of entrainment mechanisms can significantly help reduce ferroalloy losses with slag. The interfacial interaction between metal and slag and the stability of the interface between them are characterized by interfacial tension. [4] High interfacial tension promotes better separation, while the opposite is true for low interfacial tension. In metal-slag systems where surface-active elements such as sulfur, oxygen, selenium and tellurium are present, interfacial tension decreases as a result of higher mass transfer rates, leading to problems with the separation of metal and slag due to the formation of metal-slag emulsion. [5] In ferroalloys production, major elements which represent surface-active elements are sulfur and oxygen. For such systems, the thermodynamic equilibrium between ferroalloy and slag can be described by the reaction [6] : Experimentally, the interfacial tension between two molten materials is typically determined by melting materials in a furnace equipped with an X-ray camera [7] or by applying the sessile drop technique with a digital camera. [8] After recording images of the interfacial interaction between two phases, interfacial tension is obtained by solving the Young-Laplace equation (Eq. [2]) numerically, where DP is the pressure difference at the interface, c is interfacial tension, R 1 and R 2 are the principal radii of curvature, [9] which describes the relationship between interfacial tension and the shape of the interface. However, in most cases, the measurement of interfacial tension is extremely complicated due to high temperatures and complex composition of molten materials.
The present study is based on methodologies for the measurement of interfacial tension and apparent contact angles between ferroalloy and slag, which were developed and verified by the authors previously. [10,11] Interfacial interaction in synthetic FeMn-slag and SiMn-systems, both with and without sulfur addition to ferroalloy, has been investigated by combining analysis of images from a sessile drop furnace and multiphase flow simulations in OpenFOAM v6, [12] and discussed together with the assessment of the sensitivity of the results by comparing different experiments.

A. Material Preparation
Synthetic FeMn, SiMn and their corresponding slags have been prepared from pure powders for studying interfacial interactions in the sessile drop furnace. The composition of the synthetic materials has been chosen according to the composition of the industrial materials [2] as shown in Table I. The purity of chemicals used for material preparation is specified in Table II. The amount of each chemical required to produce corresponding synthetic materials has been calculated taking into account both the purity of chemicals and the composition of industrial materials and is presented in Table III.
The powders were mixed and melted separately in a graphite crucible in an induction furnace in Ar atmosphere at temperatures up to 1773 K for FeMn and 1873 K for SiMn. The holding time for preparation of FeMn and SiMn was 60 min, and for slags-5 min. After the melting, both ferroalloys and slags were ground in a ball mill and divided into batches of 50 g. Iron(II) sulfide  FeMn  78  15  -7  -----SiMn  68  12  18  2  -----FeMn Slag  ----38  23  6  23  10  SiMn Slag  ----11  23  6  43  17 powder has been added to batches of FeMn and SiMn to provide 0.33, 0.66 and 1.00 wt pct of sulfur as shown in Table IV. Thereafter, both ferroalloys and slag were remelted at the same operational parameters in the induction furnace. Note that the carbon has not been added as a raw material for melting as it is contained in the graphite crucible, which allows ferroalloys to be saturated with the required amount of carbon-7 and 2 wt pct for FeMn and SiMn, respectively.

B. Experimental Setup
The sessile drop furnace, as sketched in Figure 1, has been applied for investigating the interfacial interaction between FeMn-slag and SiMn-slag. The sessile drop furnace was equipped with a pyrometer and a C-type thermocouple for measuring temperature, and with a digital video camera (Sony XCD-SX910CR, Sony Corporation, Millersville, MD) with a telecentric lens (Navitar 1-50993D) for recording images of the molten samples with the resolution of 1280 Â 1024 pixels at one frame per second after reaching the melting point of ferroalloys and slags. Every 10 to 15 experiments, the thermocouple was calibrated by melting pure Fe in Ar and assessing its melting temperature from recorded images. The experiments were performed using graphite substrates or cups in Ar atmosphere (6 N grade) according to the experimental matrices as demonstrated in Tables V and VI. Additionally, the surface of the graphite substrates and cups was cleaned with a paper towel dipped in ethanol or acetone and then dried using compressed air.
Two experimental methods (Figure 2), were employed in this study: -Method A (Figure 3(a)), allowing to measure apparent contact angles between metal and slag.
-Method B (Figure 3(b)), allowing to determine both interfacial tension and apparent contact angle between metal and slag.
Initially, it was planned to apply only method B for studying interfacial interaction for both FeMn-slag and SiMn-slag systems, but subsequently it was found that SiMn has a poor wetting towards graphite, forming a SiMn droplet instead of a molten layer in the graphite cup as it is illustrated in Figure 4. Therefore, method A was adopted for the SiMn-slag system.
After the experiments, the ferroalloys and slags were cast in epoxy, sectioned in the centre of the slag droplet, re-cast into epoxy, polished and coated with carbon prior to analysis in EOL JXA-8500F Electron Probe Micro Analyzer (EPMA). The composition of the ferroalloy and slag phases were measured in several points and then average composition of each phase was calculated. Elemental mapping was performed for several samples to show sulfur distribution between metal and slag. Additionally, the chemical composition of ferroalloys and slags prior to experiments was determined by X-ray fluorescence (XRF) and the combustion infrared detection technique (combustion-IR). The ferroalloys were analyzed for Mn, Fe, Si, S and C, whereas slags were analyzed for MnO, CaO, MgO, SiO 2 , Al 2 O 3 and FeO.
In addition, the surface tension of FeMn, SiMn and slags was measured using the sessile drop furnace by melting ferroalloy or slag pieces on a graphite substrate. Surface tension for FeMn and FeMn slag was measured at temperature of 1723 K and at 1923 K for SiMn and SiMn slag.

C. Methodology for Measurement of Surface and Interfacial Tension
The methodology for determination of slag-metal interfacial tension is based on measurements of surface tension, followed by a comparison of geometrical features obtained from multiphase computational fluid dynamics (CFD) simulations using OpenFOAM [12] and experiments in the sessile drop furnace. The complete procedure is described in Reference 11, with a summary is given in the following for reference.
The elliptic solution of the Young-Laplace equation [14] has been applied for measurements of slag surface tension. Here, surface tension is expressed as: where g is the gravitational acceleration, q Ar is the density of Ar ð1:66 kg/m 3 Þ, q slag is the density of slag in liquid state ð3300 kg/m 3 Þ for FeMn slag and 2700 kg/m 3 for SiMn slag. [15] Values of a and b are the length of the semi-minor and semi-major axis-respectively-found by fitting an ellipse to the slag contour. The elliptic solution results in a significant error in measurements in case if the droplet has a high wettability towards the substrate (contact angle < 90 ) or if the surface of the droplet does not form a perfect circle or ellipse. Surface tension of ferroalloys was measured by a plugin for ImageJ [16] based on low-bond axisymmetric drop shape analysis (LBADSA), which allows to fit the Young-Laplace equation to images and extract parameters of droplet's contour. [17] The main output from the plugin is the capillary constant c, which is used then to calculate the surface tension via the equation: In method A, ferroalloy and slag were placed on a graphite substrate. In method B, slag was placed on top of a ferroalloy layer in contact with a graphite cup. The interaction between slag and ferroalloy before melting for method A and B, respectively, is shown in images (a) and (c), while the interaction at the molten state is shown in images (b) and (d). Please note that the roughness on the surface of the droplets is related to the formation of solid carbon particles during the melting, which will be discussed further in Sect. III.B.
where c is the capillary constant in m À2 , q metal is the density of ferroalloys in liquid state À 5612 kg/m 3 for FeMn and 4449 kg/m 3 for SiMn. [15] The apparent contact angle between SiMn and slag has been measured every 30 to 60 seconds after 30 seconds of holding time-directly from images using the open source image processing software (ImageJ [18] ).
The interfacial tension between FeMn and slag has been measured by method B approximately every 30 seconds after 2 minutes of holding time at minimum volume expansion of slag droplet to minimize the influence of volume fluctuations on the results. Method B, which is essentially based on comparing geometrical features obtained from simulations and experiments, consists of the following steps [11] : (k R ) directly from experimental images as the average size of solid particles found at the FeMn-gas and slag-gas interface. In this study, k R was up to 0.25 mm, depending on the surface roughness. (e) Calculate the total volume of the slag droplet using slag density in the molten state and weight of the slag droplet measured before experiments: where m slag is weight of the slag droplet.
(f) Calculate the visible volume of the slag droplet (V vis ) in experiments assuming that the slag droplet forms a spherical cap both above and below the FeMn-gas interface and subtracting k R from the visible height and the radius of the slag droplet: where h vis is visible height of the slag droplet and a is radius of the slag droplet. (g) Calculate the non-visible volume of the slag droplet (V nonÀvis ): (h) Calculate the non-visible height of the slag droplet (h nonÀvis ) in the experiments: (i) Calculate the non-visible height of the slag droplet in pct: (j) Compare experimental and simulation values to determine interfacial tension.
The 95 pct confidence interval for the sample mean was calculated based on the Student's t-distribution [19] : where y is the sample mean, t is the critical value found from the confidence level and degrees of freedom of the sample, s is unknown sample standard deviation and n is the number of observations-from 6 to 31 in this study. Here, s is expressed as: where y i y 1 ; y 2 ; . . . ; y n f grepresents one measured value of the sample (i.e. single observation).

A. Chemical Composition of Synthetic Ferroalloys and Slags
The chemical composition of ferroalloys before experiments was analyzed by XRF and combustion-IR and is summarized in Table VII, while the chemical composition of slags before experiments was analyzed by XRF and is given in Table VIII. Due to formation of FeMn dust and MnO 2 particles during combustion which then settle in the filter and lead to substantially lower sulfur values in the samples, sulfur content in FeMn could not reliably be determined by XRF and combustion-IR. Consequently, sulfur content in FeMn was estimated by EPMA from BSE images based on the surface area of the sulfide phase to the total area of the sample. The estimated sulfur content by EPMA is provided in Table IX.
Comparing the composition of the synthetic ferroalloys and slags with the composition of the industrial materials given in Table I, it is obvious that their compositions are close to a large extent, which indicates the correctness of the methodology used for the materials preparation in the current work.

B. Surface Tension of FeMn, SiMn and Corresponding Slags
The experimentally measured average values of surface tension by employing the aforementioned methodologies are presented in Figure 5. As it is expected for metals, FeMn and SiMn have higher values of surface tension -1.50 and 1.20 N/m, respectively, while slags  Figure 6, which gives greater variation in measurements. The observed roughness of FeMn could be attributed to a higher C content, and hence more C can precipitate or dissolve during experiments with FeMn.
In all experiments with FeMn, solid carbon particles have been observed on top of FeMn layer as illustrated in Figure 7. Their formation may be caused by different temperatures during the materials preparation and the experiments. As it can be seen from Figure 8, the carbon saturation in FeMn is estimated to be 7.4 wt pct at melting temperature of 1773 K used in the induction furnace. However, at experimental temperatures of 1623 to 1723 K used in the sessile drop furnace, the carbon saturation decreases down to 7.0-7.3 wt pct and the rest of carbon remains in solid state, which can consequently be observed on top of the FeMn layer in the experiments. A similar phenomenon of floating carbon particles on top of the FeMn melt was suggested by Hoel, [20] where it was discussed that excess carbon precipitates as graphite from the supersaturated melt as the temperature decreases. Figure 6(c) demonstrates that the amount of solid carbon precipitation on surface of the SiMn alloy is significantly lower compared to the FeMn alloy, since the melting of SiMn in the induction furnace at 1873 K and holding time of 60 minutes allowed to dissolve only %2 wt pct of carbon in the SiMn alloy and, as shown in Figure 9, this amount of carbon is completely dissolved in liquid SiMn at 1873 K.
It is worth mentioning that the evaporation of slag and metal droplets was not observed at the proposed temperatures ( Figure 6) in the experiments for measurements of surface tension. The sample size over time only increased in all experiments due to thermal expansion. For instance, the volume change of the FeMn droplet was up to 10 pct higher after increasing temperature from the melting point (% 1533 K) to 1773 K, when surface tension was measured. The given sample size in this study was chosen to reduce the effect of solid carbon particles precipitation on the surface of FeMn, as decreasing the sample size is expected to introduce more uncertainty associated with the surface roughness. On the contrary, the variation in the droplet size (e.g. an   unreasonably big droplet) will also affect surface tension, as it can be inferred from Eq. [12], where the Eo¨tvo¨s number characterizes the balance between the gravitational force and the surface tension force, [21] and therefore the surface profile of a liquid droplet. However, no surface tension change was observed in the present study either using a droplet twice smaller or the given droplet size.
where Eo is the Eo¨tvo¨s number, Dq is the density difference between two phases, D is the diameter of the droplet. High values of Eo specify that the droplet is strongly affected by the gravitational force, flattening the droplet, while low Eo values indicate that the droplet has the spherical shape. [22] As it is has been reported by Lee et al., [23] the surface tension of a pure Fe-system is 1.90 N/m, while Mn addition decreases the surface tension, [24] reaching surface tension of 1.00 N/m for a pure Mn-system without C addition. Assuming that there is no carbon present in FeMn used in the current work, which corresponds to 84 wt pct Mn and 16 wt pct Fe, the surface tension of FeMn of this composition according to Lee et al. is 1.10 N/m compared to 1.50 N/m measured experimentally for the high-carbon saturated FeMn alloy. There is no data published on surface tension of SiMn; therefore, as an analogue of the Fe-Mn    3632-VOLUME 52B, DECEMBER 2021 system, surface tension can be alternatively described only for the Fe-Si system. The similar negative trend of Si on surface tension has been observed for a Fe-Si system, [25,26] where the addition of Si to pure Fe decreases surface tension from % 1.80-1.90 to 0.70 N/m. Lee and Morita [27] studied the surface tension of a Fe-C-S system, where they found that surface tension of a pure Fe gradually decreases with sulfur addition, which is caused by a high concentration of sulfur at the surface. In the present study, even though sulfur acts as a surface-active element, there is no interaction between sulfur in ferroalloys, the graphite substrate and Ar during melting in the sessile drop furnace. In addition, the applied LBADSA methodology is not able to determine small changes in surface tension due to the uneven surface of ferroalloy droplets. These two factors can explain constant surface tension with increasing sulfur content in ferroalloys from 0 to 1.00 wt pct.
Besides that, Lee and Morita [27] showed that C addition to pure Fe on alumina or aluminium nitride substrates increases surface tension. As it can be adopted for ferroalloys studied in this work, both FeMn and SiMn, being completely saturated with carbon after melting in the graphite crucible in the induction furnace, do not react with the graphite substrate, which results in a higher surface tension compared to non-carbon ferroalloy systems.
Depending on the composition, multicomponent slags generally have surface tension in the range from 0.30 to 0.70 N/m, [28,29] which corresponds to the ranges of surface tension found in the present study.

C. Effect of Sulfur Addition to Ferroalloy-Slag Systems
The effect of sulfur content in the SiMn alloy (S SiMn ) on the average apparent contact angle between SiMn and slag has been studied at constant maximum temperature of 1873 K and constant holding time of 5 minutes and is shown in Figure 10. The increase of S SiMn from 0.02 to 0.90 wt pct decreases the average apparent contact angle from 37.8 to 29.6 . The largest change of À 6.7 is observed between S SiMn of 0.02 and 0.25 wt pct, while the change between S SiMn of 0.25 and 0.62 wt pct , and between S SiMn of 0.62 and 0.90 wt pct was only À 1.1 and À 0.4 .
The average interfacial tension between FeMn and slag changes depending upon sulfur content in the FeMn alloy (S FeMn ), as shown in Figure 11. The largest change of À 0.30 N/m is noted when S FeMn increases from 0.03 to 0.31 wt pct, which indicates that the equilibrium in the FeMn-slag-S system is reached in this range of S FeMn . The further increase of S FeMn to 0.93 wt pct decreases interfacial tension only slightly from 0.96 N/m to 0.88 N/m. However, the measurements for S FeMn of 0.31 and 0.57 wt pct have a larger deviation described by confidence intervals of AE0:09 and AE0:05 N/ m, respectively. As illustrated in Figure 12, these two experiments have significant fluctuations in surface area due to the gas evolution after 2 minutes of holding time at the maximum temperature, which most likely contributes to the variance observed in the experiments.
Sulfur, as a surface-active element, mainly concentrates at the surface or the interface and therefore the concentration of sulfur in the bulk does not play a significant role on the interfacial mass transfer, which reasonably means that the maximum concentration of sulfur at the interface is reached at S SiMn of 0.25 wt pct and S FeMn of 0.31 wt pct and the further increase of sulfur content in ferroalloys does not affect interfacial interaction in the FeMn-slag-S and SiMn-slag-S systems significantly. Suzuki et al. [30] have studied the effect of sulfur in a Fe-slag system on the dynamic change of apparent contact angle, where they found that sulfur absorbs at the Fe-slag interface and the apparent contact angle gradually decreases during reactions between metal and slag which is more pronounced with sulfur addition. Kim and Tangstad [31] studied the reduction kinetics of FeMn and SiMn slags in CO atmosphere at temperatures up to 1873 K. The authors reported that the initial sulfur content in slags changes the rate constant non-linearly, meaning that the rate constant reaches a maximum at a certain sulfur content in slag -0.29 wt pct in their work. This may explain the surface area fluctuations in the experiments with S FeMn from 0.31 to 0.57 wt pct in the given study, which are caused by higher reaction rates and thereby faster reactions between FeMn and slag.
Even though sulfur has not been added in experiment 13, sulfur is found to be evenly distributed between SiMn and slag as shown in Figure 13. This may indicate that sulfur was introduced to the SiMn-slag system from the powders or the graphite crucible during materials preparation or from the graphite substrate during the experiments. After increasing sulfur content in SiMn to 0.62 wt pct, the sulfur distribution shifts towards the slag phase and sulfur mainly concentrates in the bulk of slag ( Figure 14). The similar distribution of sulfur has been observed for the FeMn-slag-S system, in which sulfur is predominately found in the slag phase as illustrated in Figure 15. This was confirmed further by calculating the sulfur distribution in FactSage [32] (Figure 16), from which it is evident that sulfur tends to be distributed in slag, whether added to FeMn or SiMn.

D. Effect of Temperature
The effect of temperatures from 1823 to 1923 K on average apparent contact angle between SiMn and slag for S SiMn of 0.02 and 0.62 wt pct at holding time of 5 minutes is shown in Figure 17. From this figure, one can notice that temperature has almost no effect on the apparent contact angle for S SiMn of 0.02 wt pct, slightly decreasing it from 37.3 at 1823 K and 37.8 at 1873 K  to 35.6 at 1923 K, D 1823!1923 K = À 1.7 , D 1873!1923 K = À 2.2 . However, for S SiMn of 0.62 wt pct, the temperature influence is more evident, resulting in almost complete covering of SiMn by slag ( Figure 18) and in a sharp decrease of apparent contact angle from 30.0 to 5.0 with increase of temperature from 1873 to 1923 K, D 1873!1923 K = À 25.0 . Please note that the contact angle is challenging to determine from images as shown in Figure 18; however, the full dynamics observed in the recorded videos from the experiments allowed the contact angle to be determined based on the initial position of both droplets.
Similarly to the SiMn-slag-S system, temperature affects interfacial behaviour between FeMn and slag both with and without sulfur. As shown in Figure 19, average interfacial tension decreases considerably with temperature in the FeMn-slag-S system with 0.57 wt pct S, D 1623!1723 K = À 0.36 N/m, compared to the system without sulfur addition, D 1623!1723 K = À 0.21 N/m.
As it was found in other studies, [31,33] the mass transfer rate of sulfur tends to increase with temperature, resulting in more intensive reactions and therefore lower values of interfacial tension between metal and slag.  Due to the higher temperatures in experiments with the SiMn system, slag could be reduced by solid carbon, changing the initial slag composition and hence affecting the results. As found by EPMA and shown in Table X, slag composition changes after reaction with the SiMn alloy at different temperatures and, at lower temperatures, MnO reduces first.   Constant interfacial tension for the FeMn system and apparent contact angle for the SiMn system may indicate that the equilibrium in these systems has been reached and further holding does not affect the interfacial interaction. This also accords with previous observations, [30,[34][35][36] where it was concluded that apparent contact angle between metal and slag dynamically changes with holding time, decreasing down to a certain minimum during the absorption of sulfur at the metal-slag interface. Subsequently, apparent contact angle stabilizes after increasing to a certain constant value, when sulfur is desorbed from the interface into the bulk of the molten metal and slag.
The sulfur distribution has been measured after the experiment with S FeMn of 0.57 wt pct and holding time of 10 minutes ( Figure 22). It can seen by comparison with Figure 15, that the distribution of sulfur to the slag phase does not change significantly as holding time increases from 5 to 10 min, further indicating that the equilibrium has already been achieved at holding time of 5 min.  where it is clear that there is a strong indication of reactions between slag and metal during the experiments, which partially explains uncertainties in the measured values.

IV. CONCLUSIONS
Sulfur plays a major role in the separation of metal and slag in ferroalloy production due to its ability to change the interfacial energy at the metal-slag interface, which leads to the formation of metal-slag emulsion and therefore additional metal losses with slag. In this study, the influence of sulfur added to FeMn or SiMn on the interfacial interaction between ferroalloy and slag has been investigated in a sessile drop furnace by applying different methodologies for FeMn and SiMn systems and comparing statistical data calculated from experimental results.
One of the more significant findings to emerge from this study is that there is a maximum of the extent to which sulfur can change interfacial tension and apparent contact angle between ferroalloy and slag-the maximum change was found at 0.25 wt pct sulfur in the SiMn alloy and 0.31 wt pct sulfur in the FeMn alloy. For all sulfur additions to ferroalloys, it is observed that sulfur  distributes mainly to slag after reaching equilibrium and the amount of sulfur remaining in the metal phase is less than 15 pct.
It has been also noted that the effect of temperature on interfacial tension and apparent contact angle is more noticeable in ferroalloy-slag systems with sulfur addition, which can be explained by a higher mass transfer rate and a larger interfacial area in such systems.
The holding time seems to have a limited effect on both interfacial tension and apparent contact angle. Despite small changes observed for both systems, these results must be interpreted with caution, since the confidence intervals in all holding time experiments overlap greatly. These small changes in interfacial properties may indicate that equilibrium in the SiMnslag system and FeMn-slag system with and without sulfur is achieved before 5 minutes of holding time, while for the SiMn-slag-S system equilibrium is reached at 10 minutes of holding.
Solid carbon particles have been found on top of the FeMn layer and thereby the improvement of the materials preparation methodology might be necessary to reduce the uncertainty in measurements-for example, using crucibles made of other materials than graphite or chemical reagents of a higher purity. However, this might also introduce additional experimental difficulties in saturating the required amount of carbon, since in this case it has be added as a raw material. Besides, interfacial tension has not been measured for the SiMn system due to the fact that only graphite cups were used in the sessile drop furnace and a limited wettability of SiMn towards graphite. Therefore, experiments with cups made of different materials can be a further development of the current methodology.

ACKNOWLEDGMENTS
This publication has been funded by the Research Council of Norway (KPN Project, 267621)

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APPENDIX A
See Appendix Tables XI and XII.