Statement of Novelty

Thus, very limited studies have been conducted to investigate FeCr slag feasibility in high temperature applications, such as in refractory products. This study addressess FeCr slag use as aggregate in refractory castables by investigating comprehensively refractory castables thermo-physical and mechanical properties. To authors’ knowlewdge, there is a lack of information of ferrochrome slag utilizing refractory materials behaviour at elevated temperatures. For this reason, mechanical and thermal properties of ferrochrome slag based refractories were evaluates also at high temperatures, resulting novel information about their high temperature behaviour.


Globally 1.6 Gt of steel was produced in 2014 creating 250 Mt of steel slag as residue [1]. Disposal of the slag is the major issue for steel industry and the utilization of steel slags has been under active research in many years [2]. Most of the slag (50%) is used for road projects, sintering, iron making and recycling within the steel plant [3]. High Carbon Ferrochrome (HCFeCr) is the most common alloying material used for the production of different grades of stainless steel. World high carbon ferrochrome production was 6.0 Mt in 2005 and the generation of ferrochrome (FeCr) slag, the residue generated from HCFeCr production, amounted 1.1–1.6 t/t FeCr depending on feed materials [4]. Numerous studies are available in the literature about FeCr slag utilization in road and civil construction purposes, such as coarse aggregate in concrete applications and pavement layers [5,6,7,8,9], partial substitution of fine aggregate sand in concrete [10, 11] and raw material in bricks [12]. Kumar et al. [13, 14] have reported FeCr slag use as aggregate in refractory castables replacing partly commercial aggregates use. They reported 50 wt% of slag use together with 35 wt% of calcined bauxite in [13] and 45 wt% of slag and 40 wt% of calcined bauxite use in [14]. Results for such refractories disclosed compressive strengh values as high as 60 MPa, indicating the potential for ferrochrome slag use in refractory products. Thus, very limited studies exist of FeCr slag feasibility in high temperature applications. This study addresses FeCr slag use as aggregate in refractory castables by investigating comprehensively refractory castables thermo-physical and mechanical properties. To authors’ knowlewdge, there is a lack of information of ferrochrome slag utilizing refractory materials behaviour at elevated temperatures. For this reason, mechanical and thermal properties of ferrochrome slag based refractories were evaluates also at high temperatures, resulting novel information about their high temperature behaviour.

Refractories are ceramic materials that withstand a variety of harsh conditions, including high temperatures, corrosive liquids and gases, abrasive wear, and mechanical and thermal stresses [15]. They are indispensable to all high temperature processes in the production of metals, cement, glass and ceramics as in lining materials for furnaces, kilns, incinerators, and reactors. An enormous variety of refractories exists, designed to meet the temperature and process requirements of each application. Refractory materials are designed so that their properties will be appropriate for the application [16]. Refractory industry is heavily dependent on raw material imports and, within the last years, there has been significant increase in material prices [17]. For refractory industry, the need to secure the availability of raw materials at competitive price has created a strong incentive for exploration of alternative sources of raw materials to substitute virgin raw materials [18] as well as to develop recycling of spent refractories [19].

This paper reports the characteristics of ferrochrome slag and its feasibility as aggregate in refractories aiming to substitute virgin raw materials. Refractory castable specimens were formulated with ferrochrome slag as an aggregate and commercial calcium aluminate cement as a binder. Objective in this study was to prepare refractory specimens with a maximum slag utilization but simultaneously to sustain good properties, comparable to those of virgin raw material products. The testing of refractory properties, in most cases, indicate the performance of a refractory in actual application. Hence, appropriate testing of refractories for predicting properties, closely simulative to their applications, is of great importance [16]. As this study aimed to determine the feasibility of ferrochrome slag to substitute the virgin raw materials in refractories, the effect of slag on refractory specimen properties was investigated and compared with conventional, commercial reference material targeted for similar applications. Mechanical and thermo-physical properties of the cured, dried and sintered specimens were characterized in terms of cold crushing strength, bulk density, porosity, thermal expansion, specific heat capacity and thermal conductivity. Mechanical and thermal properties were evaluated also at high temperatures. In addition, mechanical properties were defined for FeCr slag based refractories exposed to corrosive gaseous atmosphere.

Materials and Experimental Procedures

Raw Materials

In this study, ferrochrome slag, originating from high carbon ferrochrome production, was used as aggregate and commercially available calcium aluminate cement (Secar 71 provided by Kerneos) was used as a hydraulic binder in refractory castable specimen formulation. Another steel industry slag, electric arc furnace, EAF, slag originating from carbon steel production was used as fine fraction for castables. As a reference, commercial refractory castable Calde Flow LF50A provided by Calderys was used. Table 1 shows approximate chemical compositions of the raw materials, the total oxide concentrations measured with X-ray fluorescence (XRF) method.

Table 1 Approximate chemical composition of the raw materials (%)

Particle packing optimization of refractory castables covers the selection of right size and amount of various particles [20]. The particles size distribution is selected to fill up the voids between large particles with smaller particles and thus to increase the particle packing density. In this study, Elkem Materials Mixture Analyser Software (EMMA) was used for optimal particle packing calculations in order to formulate the optimal recipes with the right size and amount of various particles using distribution coefficient (q) value of 0.30. Particle size distribution optimization was based on packing models and curves developed by Andreassen [21]. The optimization curves were combined in such a way that the total particle size distribution of the mixture is closest to an optimum curve. In this study, maximum slag utilization was targeted and the FeCr aggregate percentage of 81.8 wt% was kept constant throughout the study. The ratio between cement and the aggregates was locked to 1:4.5 on weight basis. The batch compositions listed in Table 2 were formulated. The composition of Castable1 was formulated using only FeCr slag as aggregate and commercial cement as binder. Castable2 was prepared using 0.15 wt% commercial dispersant (provided by BASF, Castament [22]) in order to evaluate the effect of dispersant use on aggregate binder compatibility and hence strength values. BASF Castament dispersants consisted of polymers based on polyethylene glycol. They are developed to disperse calcium aluminate cement particles and aggregates in order to improve the rheological properties of castables in refractory applications [22]. In the compositions of Castable3 and Castable4, part of the commercial cement (10% and 20%) was replaced by fine EAF slag fraction. Water to cement ratio was experimentally locked to 0.51 for Castables1, 3 and 4 and to 0.44 for Castable2.

Table 2 Batch composition of slag based specimens as wt%

Preparation of Refractory Castable Specimens

The FeCr slag fine aggregates 0–4 mm were selected for study. At first, the FeCr slag was dried for 7 h at 105 °C and sieved to the particle size below 4 mm. EAF slag was milled by means of the disintegrator DESI 15/16 C to the particle size below 75 µm. Refractory castable specimens were prepared according to standard EN 196-1 [23]. A standard steel mould with the size of 40 × 40 × 160 mm3 was used for mixed compositions. Castable were perepared by mechanical mixing and compacted in a mould using a standard jolting apparatus as described in standard. Specimens were first cured for 24 h in the moulds in a curing cabinet (RH > 95%) at room temperature. Then the specimens were removed from the mould and left for another 24 h in the curing cabinet in a plastic bag at room temperature. After that, specimens were moved to drying oven for 7 h at 105 °C. The dried specimens were then sintered in air atmosphere by slowly heating them to 540 °C and kept at this temperature for 3 h, then heated to 1200 °C and kept there for another 3 h.

Characterization Methods

FeCr slag was characterized by microstructural and compositional studies as well as thermal analyses to find out its characteristics. Microstructural investigations were performed using a field-emission scanning electron microscope (FESEM Zeiss ULTRAplus) equipped with an energy dispersive spectrometer (EDS, INCA x-act silicon-drift detector (SDD), Oxford Instruments). The identification of crystalline phases was done by using an X-ray diffractometer (XRD, Empyrean, PANanalytical B.V., ALMELO, Netherlands) with Cu-Kα radiation source, and analysed using HighScore Plus software. The thermal behaviour was studied using thermogravimetric analysis (TGA, Netzsch STA 449 F1 Jupiter) giving also a simultaneous Differential Scanning Calorimetry (DSC) signal. The measurements were made in air and argon atmospheres at a heating rate of 10 °C/min.

In order to evaluate the strength behaviour for slag-based refractory specimens, six specimens were prepared from the Castable1 composition mixture, and their compressive strengths were recorded after chosen steps. The preparation of six specimens took place on day 1. After 24 h of curing in the moulds placed in the curing cabinet, specimens were removed from moulds and the compression test was carried out for one of the six specimens, with the strength value being recorded as the 1-day compressive strength (step1). On day 2, five of the specimens were left in the curing cabinet in a plastic bag. One of the five specimen was kept separately in the curing cabinet for the measurement of 7-day compressive strength (step2). On day 3, four remaining specimens were moved to drying oven where they are kept for 7 h at 105 °C. At the end of the day after drying, one of the specimens was subjected to the determination of compression strength at 105 °C (step3). On day 4, three of the dried specimens were slowly heated to 540 °C and kept at the temperature for 3 h. On day 5, one specimen from day 4 was heated to 1000 °C, the second specimen was heated to 1200 °C, and the third specimen from day 4 was used for the compression test at 540 °C (step4). On the next day, the cooled specimens were subjected to compression strength determination, and their strength values were recorded for 1000 °C (step5) and for 1200 °C (step6).

The microstructural, physical, mechanical and thermal properties of cured, dried and sintered refractory castable specimens were characterized. Metallographic cross sections were produced by casting the cut sections of specimens in Epofix cold setting resin under low pressure. The castables were then ground and polished. An OLYMPUS digital camera was used for photographing of cross sections. The cross sections were also analysed using FESEM, for which the castables were carbon coated for electrical conductivity. Apparent solid density, bulk density and open porosity of the specimens were investigated according to Archimedes principle following the ISO18754 standard. Thermal expansion coefficient α for the specimens was measured by dilatometry using a Netzsch Dilatometer DIL 402C. The used sample size for the measurements was rectangular 25 mm × 5 × 5 or cylindrical, 25 × 5 mm diameter, cut by a diamond saw, and the heating rate was 5 °C/min. Specific heat capacity and thermal conductivity were measured by laser flash analysis (LFA 457 Microflash, Netzsch) in argon atmosphere for the samples of the size 10 × 10 × 2 mm3. Samples were prepared by a hollow drill and measured in the temperature range from 21 °C up to 1000 °C. Cold crushing strength of the specimens was tested based on the standard EN 196-1 [23] using uniaxial strength tester. The compression tests were carried out at the constant load rate of 2.4 kN/s as indicated in the standard. For high temperature mechanical tests, cubic samples were prepared from sintered castables. To obtain the desired sample size (10 × 10 × 10 mm3), a diamond saw with a blade thickness of 0.5 mm was used using a slow cutting speed. The tests were done under argon atmosphere at 1200 °C, with an initial pinchload of − 0.05 kN and a heating rate of 10 °C/min. Once the temperature was reached, compression was performed at a displacement rate of 0.2 mm/min. All the measurements were done in furnace using an Instron frame with a 4 MPa loading cell. Exposure tests for the samples of size 20 × 20 × 2 4 mm3 were performed in HCl/SOx gas mixture with 15% humidity at 700 °C temperature for 168 h, after which the strength values were recorded for the exposed specimens.

Results and Discussion

Characterization of the FeCr Slag

Figure 1 presents X-ray diffraction (XRD) pattern for FeCr slag. Spinel phases (chromian, ferroan) (Mg)(Al,Cr)2O4 appeared as main crystalline peaks. Other identified phases included forsterite Mg2SiO4 and enstatite MgSiO3. Additionally, the XRD spectra showed a slight increase in the overall intensity of the curve at low 2θ values which indicates the presence of an amorphous phase.

Fig. 1
figure 1

XRD pattern for the ferrochrome slag

Figure 2 shows FESEM (AsB) micrographs of the FeCr slag cross section with two different magnifications. Microstructural examinations revealed clearly that microstructure of the slag includes several crystalline phases surrounded by an amorphous glassy phase. Elemental maps disclosed that aluminium is concentrated, together with chromium and magnesium, on larger separate quadrilateral-shaped crystals, most likely spinel (Mg)(Al,Cr)2O4 phase. Magnesium was concentrated on elongated needle-like crystals together with silicon, most likely being forsterite, Mg2SiO4, or enstatite, MgSiO3, phases detected by XRD analyses. Iron was detected in separate spots, seen in the brightest contrast in SEM images. Crystalline phases were surrounded by silicon-rich amorphous glass phase, seen in darker contrast in SEM images. The shape of the XRD curve supports the presence of amorphous phase besides the crystalline phases. The mineralogy of FeCr slag was characterized in detail by Makkonen and Tanskanen [24] who have suggested similarly that common phases in the slag are Fe–Mg–Cr–Al-spinels, forsterite (Mg2SiO4), Mg-silicates and metal droplets. With fast cooling rates, the slag is not totally crystalline, with amorphous glass phase being solidified between the grains. The amount of amorphous glass phase depends on the cooling rate being typically between 60 and 70% in FeCr slag [24].

Fig. 2
figure 2

FESEM images (AsB) of the cross-section of FeCr slag with different magnifications

Figure 3 shows the TG/DSC measurement curves of the FeCr slag measured in argon and air atmospheres. In both atmospheres, an exothermic peak was detected in DSC curves above 900 °C similarly than in the study Zelic [5]. Additionally, in air, the weight loss curve started to increase slightly above 400 °C showing also a small exothermic peak in the DSC curve. In air, the weight loss curve continued to increase with increase in temperature, relating most probably to metal iron droplets oxidation detected in microstructure observations. In both atmospheres, peaks observed in DSC curves above 1200 °C were probably related to liquid slag phase formation, with temperature increases increasing the content of liquid phase. In the study by Zelic [5] FeCr slag melting point was reported to fall in the temperature range of 1200–1400 °C. The liquid phase formation at high temperatures restrains the use of FeCr slag-based materials for structural applications. Refractory systems should be designed in such a way that the maximum temperature attainable in the system is lower than the softening or melting temperature of the refractory ingredients: the binder and the aggregates [16]. Thus these results suggest that maximum service temperature for these type of novel FeCr slag based refractory material is 1200 °C.

Fig. 3
figure 3

TG/DSC curves for FeCr slag a in argon and b in air

Properties of the Sintered Refractory Specimens

Figure 4 shows macroscopic cross-sectional images of sintered refractory castable specimens for (a) Reference (b) Castable1 (c) Castable1 after reheating to 1260 °C and (d) Castable1 after reheating to 1320 °C. Images revealed that both the Reference and Castable1 specimens showed typical refractory material cross-sections, including aggregates and surrounding binder phases. Reheating tests for sintered Castable1 specimens up to temperatures 1260 °C and 1320 °C were made in order to investigate the liquid phase formation which was observed in DSC curves for FeCr aggregates. Reheating to 1320 °C revealed clearly the melting of both slag aggregates and surrounding binder phases, which strengthens the observation of maximum service temperature in DSC curves.

Fig. 4
figure 4

Macroscopic images of sintered refractory specimen cross sections a Reference, b Castable1, c Castable1 after reheating at 1260 °C and d Castable1 after reheating at 1320 °C

Figure 5 shows FESEM images of sintered cross-sectional specimens of (a) Reference and (b) Castable2. FESEM micrographs revealed that for the Reference, the compatibility between the binder and the aggregates is good, as charged based on the sharp phase interfaces in Fig. 5a. This is likely a result from long development and surface optimization work for commercial product. For slag-based Castable2 specimen (Fig. 5b), clear cracks at the binder-aggregate interfaces were detected. However, the binder was evenly distributed between the aggregates of different size fractions.

Fig. 5
figure 5

FESEM cross-sectional micrographs of sintered specimens a Reference, b Castable2

Strength Development Curves

Figure 6 shows strength development curve for Castable1 composition mixture as a function of temperature. Ceramic bonded or fired refractories are formed at high temperatures using binders and a sintering process [19]. As observed at 1000 °C no ceramic bonding has not yet developed. At 1200 °C temperature, higher strength values suggested that ceramic bonds have been formed and full strength of refractory castables has been achieved.

Fig. 6
figure 6

Strength development curve of slag based Castable1 mixture composition

Cold Crushing Strengths

The cold compressive strength or cold crushing strength (CCS) of a refractory material is an indication of its suitability for the use as refractory. It is a combined measure for the strength of the aggregate grains and the bonding system [16]. CCS values recorded for sintered specimens are presented in Fig. 7. The results are average of four specimens. It can be observed that the best performing slag-based Castable2 showed average CCS value of 91 MPa. Strength value was clearly below the strength recorded for the commercial refractory reference material, 149 MPa, but notably higher than the highest strength value, 60 MPa, reported in the studies by Kumar et al. [13, 14] for FeCr slag-utilizing castables. According to CCS values, the use of dispersant (in Castable2) increased the average compressive strength value from 79 (Castable1) to 91 MPa (Castable2). Commercial dispersant (BASF Castament) has been developed to disperse calcium aluminate cement particles and aggregates in order to improve the rheological properties of castables in refractory applications [22]. The differences between the performance of Castable2 and the Reference specimen may be explained by the still poorer compatibility of the binder and aggregate phases of Castable2, as evaluated based on the phase interface appearance (Fig. 5) although the recorded strength values as high as 91 MPa indicate that the strength of the aggregate grains and also of the bonding system are at the acceptable level. By further improving the binder-aggregate compatibility with optimal additives, it can be assumed that even higher strength values may be reached. According to CCS results, it seems that 10% cement replacement by fine EAF slag (Castable3) is possible, still keeping almost the same average strength level for the castables, 75 MPa vs. 79 for Castable1. The higher cement replacement (Castable4) resulted in lower average strength value of 71 MPa.

Fig. 7
figure 7

Cold crushing strengths of slag based-castables and the Reference

In recent years, more importance has been given to high-temperature strengths of refractories rather than cold strength values, since refractories are used at elevated temperatures [16]. Figure 8 shows the compressive strengths of sintered slag based castables and the Reference measured at the temperature of 1200 °C. Recorded strengths at 1200 °C were one tenth of corresponding value measured at room temperature. Also at 1200 °C the highest average strength value for slag-based castable was obtained for Castable2, 9.2 MPa, followed by Castable 1 (6.0 MPa). Strength results measured at 1200 °C revealed more clearly that cement replacement by fine EAF slag decreased the strength values. 10% cement replacement by fine EAF slag (Castable3) decreased the average compressive strength to 4.9 MPa and 20% cement replacement (Castable4) even lower, to 3.1 MPa.

Fig. 8
figure 8

Compressive strengths measured at 1200 °C

Apparent Solid Density, Bulk Density and Open Porosity

The values of apparent solid density, bulk density, and open porosity for slag-based castables and the Reference are shown in Table 3. The results are average of three samples. Typically, the values of density and porosity are used to recommend the refractories for specific applications [16]. In general, the higher the density, the lower the porosity and also, other physical properties, such as strength, are typically related to the density and porosity values. Table 3 shows that bulk density values were of the same order for slag-based castables and the commercial Reference, around 2.35 g/cm3. These values are typical for the alumino-silicate-based, dense refractory castables used as structural components in heat-treatment furnaces and kilns [16]. The Castable2 showed a slightly higher density value of 2.39 g/cm3 but featured also the highest variation in the values, which could partly explain the result. Nevertheless, for the best performing (highest strength) slag-based castable, Castable2, the open porosity value of 17.3% was of the same order with the commercial Reference, 16.1%. For other slag-based castables, the porosity values were approximately 20% (Castable1 and Castable3; or even higher (22% for Castable4). Thus by increasing the cement replacement with fine EAF slag fraction, the porosity is increased and the density values of the castable are lowered.

Table 3 Apparent solid density, bulk density and open porosity of refractory specimens

Thermal Expansion

Figure 9 shows the linear thermal expansion of sintered specimens measured by dilatometry. Thermal expansion coefficients, α, of the specimens were determined in the temperature interval from room temperature up to 1100 °C. Most refractory materials expand when heated and thus, when refractories are installed at room temperature, the whole structure expands and tightens up when heated [16]. Figure 9 shows that all the FeCr slag-based specimens exhibited linear expansion and the recorded thermal expansion coefficient values were at the level comparable to those for the Reference.

Fig. 9
figure 9

Thermal expansion of sintered specimens measured by dilatometry

Specific Heat Capacity and Thermal Conductivity

Figures 10, 11 and 12 show thermal diffusivity, thermal conductivity and specific heat capacity as a function of temperature for the sintered specimens. In all cases, thermal diffusivity values in Fig. 10 revealed a slight decrease with increase in temperature. Slag-based castables featured somewhat lower thermal diffusivity values as compared to commercial Reference, for which the values ranging between 1.3 and 0.7 mm2/s were obtained. Among the slag-based castables, the thermal diffusivity values closest to the commercial reference were recorded for Castable1, ranging from 1.1 to 0.5 mm2/s. The thermal diffusivity values for the slag-based Castable2 (with the best strength properties) showed the lowest thermal diffusivity values, from 0.8 to 0.4 mm2/s.

Fig. 10
figure 10

Thermal diffusivity measured as function of temperature for slag-based castables and Reference

Fig. 11
figure 11

Thermal conductivity measured as function of temperature for slag based castable and Reference

Fig. 12
figure 12

Specific heat capacity as function of temperature for slag-based castables and the Reference

Thermal conductivity is a measure of the refractory materials’ ability to conduct heat from the hot to the cold face when it is exposed to high temperatures [16]. Low thermal conductivity values implies good thermal insulation capability for refractory materials. Typically when thermal insulation is needed for refractory material, insulating refractory materials are formulated for low relative thermal conductivity and not for strength resistance. The majority of insulating castables are alumino-silicate- based or high alumina castables, having densities between 0.4 and 1.45 g/cm3 and corresponding porosities of 45–85%. Thus insulating castables show much lower densities and higher porosities than dense castables. Generally when density increases and porosity decreases, thermal conductivity will increase [16]. Thermal conductivity values shown in Fig. 11 disclosed a slight overall decrease in with a shift towards higher temperatures. Slag-based Castable2 exhibited the lowest thermal conductivity values, from 1.3 to 0.9 W/mK, which were much lower than for the commercial Reference (2.4–2.1 W/mK). However, all slag-based castables showed thermal conductivity values lower than the Reference. Thermal conductivity values of slag-based Castable2 are comparable to values shown in literature for alumina based insulating castables which show thermal conductivity value of 1.2 W/mK at 200 °C but have much lower density value of 1.2 g/cm3 [16]. These results indicate a good thermal insulation capability for FeCr slag based castables and their suitability in the use as aggregate in refractory castables for insulation purposes and simultaneously having sufficient strength for structural component also. Lower thermal conductivity values for FeCr slag compared with natural material granite has been reported also by Niemelä and Kauppi [4] for civil engineering and road construction uses.

The values of specific heat shown in Fig. 12 revealed a slightly increasing values with rise in temperature. Similar results were obtained for EAF slag reported in the literature [25].

Exposure Tests for Corrosive Atmosphere

Corrosion resistance is one of the most important characteristics of refractories, thus the test conditions have to be designed so that they closely simulate the conditions that the refractories experience during the use [16]. Thermogravimetric analyses of the FeCr slag-based refractories indicate that their maximum service temperature is 1200 °C. Thus in common metallurgical processes that operate at temperatures above 1200 °C, direct exposure to molten metal and slag should be avoided. However, potential applications may involve exposure to gaseous atmosphere, the temperature of which is typically lower than that of liquid phases. For that reason, corrosion tests were performed to predict the behaviour of FeCr based castables in acidic gaseous atmosphere. During the test procedure, samples were exposed to the gas mixture of 15% humidity and HCl/SOx at 700 °C temperature for 168 h. With visual inspection, no corrosion effects were seen on the surface of the test samples after the exposure. Mechanical tests were performed for the exposed corrosion samples in order to evaluate the effect of corrosive atmosphere on mechanical properties. According to results, corrosion exposure caused no effect on strength values—neither for the slag-based castables nor for the commercial reference. These investigations indicate that the resistance to acidic gaseous atmosphere for FeCr slag based materials is at least at comparable level to the commercial materials.


Refractory castable specimens were formulated using ferrochrome slag as an aggregate and commercial calcium aluminate cement as a binder. Mechanical and thermo-physical properties of the cured, dried and sintered specimens were characterized. The effect of FeCr slag on the properties of refractory specimens was investigated and compared with conventional, commercial reference material targeted for similar applications. From the findings of the study, the following conclusions can be drawn:

  • The liquid phase formation above 1200 °C limits the FeCr slag use as aggregate in refractory castables, thus the maximum service temperature for these novel slag-based refractory materials is 1200 °C.

  • Cold crushing strength value of FeCr slag-containing specimens was as high as 91 MPa.

  • FeCr slag-based specimens sustained their mechanical strength also at high temperatures, with the mechanical strength values at 1200 °C being as high as 9 MPa.

  • Thermal properties of the FeCr slag based specimens were even better than those of commercial refractory reference, showing thermal conductivity values as low as 1.3 W/m K.

  • FeCr slag-based castables exhibited linear thermal expansion and a low thermal expansion coefficients as low as αRT−1100 °C = 8.6 x 10–6 1/K.

  • FeCr slag-based castables were exposed to corrosive gas mixture with 15% humidity and HCl/SOx at 700 °C for 168 h. With visual inspection, no corrosion effects were seen on the surface of the test samples. Corrosion exposure caused no effect on strength values.

Results suggested the feasibility of ferrochrome slag to be used as an aggregate raw material for refractory materials up to temperatures of 1200 °C in air and in acidic gaseous atmosphere up to 700 °C to substitute virgin raw materials. Possible applications for this kind of novel refractory materials are, e.g., insulating secondary layers or bottom zones in metallurgical processes up to 1200 °C. A direct contact to molten metal in steel industry must be avoided, but they are applicable as, e.g. floorings when exposed only to occasional melt droplets.