3.1. Effect of Basicity on Liquid Amount of Sinter
The liquid phase amount of the sinter with different basicity values was calculated using the FactSage 7.1 (Thermfact/CRCT and GTT-Technologies, Montreal, Canada and Aachen, Germany). The basicity of the sintering raw material was reduced from 1.9 to 1.7 in Groups 1–3 of the experimental scheme, which indicated the effect of the acidic oxide SiO
2 on the liquid phase amount of the sinter. The basicity of the sintering raw material increased from 1.9 to 2.1 in Groups 1, 4, and 5 of the experimental scheme, which indicated the effect of the basic oxide CaO on the liquid phase amount of the sinter. The calculation results are shown in
Figure 1.
As shown in
Figure 1, at a temperature of 1250 °C, the liquid phase region of the CaO-SiO
2-FeOx-Al
2O
3-MgO system is mainly located in the direction of SiO
2 in the center of the phase diagram, and the area is small. When the temperature increases to 1275 °C, a liquid phase region rich in Fe
2O
3 appears on the CaO-Fe
2O
3 line, and the sintering liquid phase region increases gradually. When the temperature reaches 1325 °C, the liquid region fuses into a whole, and the area increases gradually. In
Figure 1, Lines a, b, and c are isobaric lines of 1.7, 1.9, and 2.1 basicity, respectively. Points A, B, and C are the corresponding composition points of the sintering material with different basicity values. Points E, E′, and E″ are the intersection points of the 1.7 basicity line with the isotherms for 1350, 1325, and 1300 °C, respectively. Points G, G′, and G″ are the intersection points of the 2.1 basicity line with the isotherms for 1350, 1325, and 1300 °C, respectively. Points F, F’, and F’’ are the intersection points of the 1.9 basicity line with the isotherms for 1350, 1325, and 1300 °C, respectively. The liquid phase amount of the sinter with different basicity values was compared using the phase diagram lever principle. The basicity of the sinter material decreased from 1.9 to 1.7 with an increase in the SiO
2 content; that is, the isobaric line moved from b to a. As shown in
Figure 1, the lengths of AD and BD remained essentially unchanged; however, the segment AE (E′ or E″) was apparently longer than BF (F′ or F″). Therefore, according to the lever principle, with a decrease in the basicity, the liquid phase amount of the sintering material decreases; hence, its liquid formation ability decreases. With an increase in the CaO content, the basicity of the sintering material increased from 1.9 to 2.1; that is, the isobaric line moved from b to c. As shown in
Figure 1, the lengths of BD and CD remained essentially unchanged; however, the length of CG (G’ or GG′) was apparently smaller than that of BF (F′ or F″). Therefore, owing to the lever principle, with an increase in the basicity, the liquid production of the sintering material increased. The increase in the CaO content improved the liquid formation ability of the sintering material.
To precisely determine the effect of the basicity on the mineral composition and liquid phase amount of the sinter material, the mineral composition and liquid phase amount were calculated using the Equilibrium module of the FactSage 7.1. The calculated results are shown in
Figure 2.
As shown in
Figure 2, the liquid amount in the sinter increased with the temperature. When the basicity of the sintering material decreased from 1.9 to 1.7, the liquid amount decreased gradually. In particular, when the basicity was 1.7, the liquid formation temperature of the sinter increased from 1137.7 to 1202.8 °C, and the liquid amount decreased from 31.05% to 25.54% at 1300 °C. The reason for this result is that when the basicity of the sinter mixture decreased from 1.9 to 1.7 because of the reduction in the content of Ca
2+ in the sinter material, the precipitation of calcium ferrite-phase minerals was restrained during the sintering process, and the precipitation of calcium magnesium olivine minerals, calcium silicate minerals, and spinel minerals was promoted. This reduced the liquid phase amount and affected the sinter properties. When the basicity of the sinter increased from 1.9 to 2.1, although the initial temperature of the formation of the liquid phase was 1137.37 °C, the sintered liquid phase amount increased. At 1300 °C, the liquid phase amount increased from 31.05% to 40.30%, and the increase in the sinter basicity was beneficial to the formation of the liquid phase. The reason for this result is that when the basicity increased from 1.9 to 2.1, the Ca
2+ content in the sinter material increased, which promoted the precipitation of calcium ferrite minerals and inhibited the higher melting point of calcium magnesium olivine minerals. Calcium silicate and iron feldspar were precipitated. Hence, the liquid amount of the low-melting point mineral transition increased. The calculation results for the Equilibrium module were consistent with the liquid region calculated using the Phase Diagram module, and the increase in the basicity of the sinter material was beneficial to the formation of liquid. Hence, the amount of biomass fuel can be increased by increasing the basicity of the sinter material.
A DSC experiment involving sintering materials with different basicity values was performed using a differential thermal analyzer. The differential thermal curves of the sintering materials with basicity values ranging from 1.7–2.1 are shown in
Figure 3.
As indicated by
Figure 3 and
Table 2, the endothermic peaks of the sintering material appeared at approximately 450 and 1200 °C, indicating that endothermic reactions occurred at all the aforementioned temperatures. CaO had strong hygroscopicity, so it reacted with water in air to form Ca(OH)
2 in the mixing process. The first endothermic peaks of DSC was that Ca(OH)
2 decomposed when the temperature increased to approximately 450 °C. When the temperature increased to approximately 1200 °C, the low-melting point mineral calcium ferrite was formed as a result of the reaction between CaO and Fe
2O
3, leading to a large endothermic peak in the curve. The low-temperature sintering mainly indicates that a sufficient liquid phase was produced at a relatively low temperature; hence, the liquid formed at 1200 °C reacted to a certain extent with the melting heat absorbed by the low-melting point mineral at this temperature. Comparing the DSC curves of different sintering materials revealed that with a decrease in the basicity, the endothermic peak temperature and endothermic peak area decreased. This is because with the decrease in the basicity, the probability of the reaction between CaO and Fe
2O
3 decreased, the endothermic peak temperature was delayed, and the amount of the calcium ferrite phase decreased because of the reduction in the CaO content. The decrease in the area of the endothermic peak of DSC was consistent with that of the FactSage 7.1 calculation. Hence, the basicity of the raw material should be increased for the low-temperature sintering process.
According to the experimental scheme described in
Table 1, the melting properties of sintering raw materials were tested using a high-temperature melting property tester. The melting property can reflect the influence of the basicity on the liquid phase formation ability of sintering raw materials. Additionally, the simulation results were verified.
As shown in
Figure 4, with a decrease in the basicity, the T10% increased from 1180 to 1231 °C, and the initial melting temperature of the sintering raw material increased. As the temperature increased, the sintering raw material started to shrink continuously. When the shrinkage rate reached 50%, the hemispheric temperature increased from 1358 to 1392 °C, and when the shrinkage rate reached 80%, the melting temperature of the sintering raw materials increased from 1372 to 1452 °C. The high basicity was beneficial to the fluidity of the sintering liquid phase and promoted the formation of the sintering liquid phase in the melting-property experiment. The experimental results were consistent with the results of the FactSage 7.1 thermodynamic simulation.
3.2. Effect of MgO Content on Liquid Amount of Sinter
The liquid amount of sinter with different MgO contents was calculated using the FactSage 7.1. The MgO content of the sintering material increased from 1.0% to 3.0% in Groups 1, 6, and 7 of the experimental scheme, which revealed the effect of the MgO content on the liquid amount of the sinter at different temperatures. The calculation results are shown in
Figure 5.
As shown in
Figure 5, when the MgO content increased from 1.0% to 3.0%, the liquid region of the CaO-SiO
2-FeOx-Al
2O
3-MgO system began to shrink and move toward SiO
2, and the liquid phase region shrank. When the MgO content reached 3.0%, the liquid region near the line of CaO-Fe
2O
3 shrank, and the high-basicity liquid region gradually disappeared. Line a is the isobaric line of 2.0 basicity, and point A is the composition point of the sintering material. Point C (D, E, F, G, or H) is the intersection of the isobaric line and the liquid phase line of the CaO-SiO
2-FeOx-Al
2O
3-MgO system. The liquid phase amounts of the sinter with different MgO contents were compared using the phase diagram lever principle. As shown in
Figure 5a–c, with an increase in the MgO content, the length of AB remained substantially unchanged. However, the length of AC (D, E, F, G, or H) gradually increased, even a portion of the intersection disappeared. Therefore, according to the lever principle, with the increase in the MgO content in the sintering material, the formation of the liquid phase was inhibited.
To precisely determine the effect of the MgO content on the mineral composition and liquid phase amount of the sinter material, the mineral composition and liquid phase amount were calculated using the Equilibrium module of the FactSage 7.1. The calculation results are shown in
Figure 6.
As shown in
Figure 6, the liquid content of the sinter increased with the temperature. The increase in the MgO content in the sinter material from 1.0% to 3.0% had no effect on the initial temperature of the liquid phase formation of the sinter. The liquid phase formation temperature was 1137.7 °C at an oxygen partial pressure of 5 × 10
−3 atm. With an increase in the MgO content, the amount of the sintered liquid phase decreased. In particular, at 1250 °C, the amount of the sintered liquid phase decreased from 26% to 7%. The calculation results of the Equilibrium module were consistent with those for the phase region obtained using the Phase Diagram module. The increase in the MgO content in the sinter material inhibited the liquid phase formation of the sinter. This may be because the increase in the MgO content increased the content of free Mg
2+ and Mg
2+ in the mono-minerals, calcium ferrite phase, and CaSiO
3, promoting the formation of spinel minerals. Hence, it was not conducive to the formation of the sintered liquid phase. In sintering with biomass fuel, the MgO content in the sinter mixture should be minimized, and the amount of biomass fuel should be maximized.
As indicated by
Figure 7 and
Table 3, two endothermic peaks were observed for the sintering materials with different MgO contents at 450 °C and 1200 °C, followed by the decomposition of Ca(OH)
2 and the formation of the liquid phase of calcium ferrite. Comparing the endothermic peak temperature and the area of the sintering material with different MgO contents at approximately 1200 °C reveals that with an increase in the MgO content, the peak temperature of the calcium ferrite formation in the sintering material increased, and the heat absorption decreased. The results of the DSC experiment and FactSage 7.1 calculations indicated that Mg
2+ can promote the formation of a high melting point mineral. Therefore, the MgO content in the sintering material should be controlled under the condition of low-temperature sintering.
According to the experimental scheme described in
Table 1, the melting properties of the sintering raw materials were evaluated using a high-temperature melting property tester. The melting property can reflect the influence of the MgO content on the liquid phase formation ability of sintering raw materials. Additionally, the simulation results were verified.
As shown in
Figure 8, the T10% increased with the MgO content in the sintering raw material, indicating that the increase in the MgO content improved the initial melting temperature of the sintered mixture. When the shrinkage rate increased to 50%, the shrinkage temperatures for MgO contents of 1.0% and 2.0% in the sintered mixture were similar, indicating that a small amount of MgO inhibited the formation of the low-temperature liquid phase. However, it had little effect on the liquid phase formation ability of the sintered mixture at a higher temperature. When the MgO content increased to 3.0%, the temperature of the sintered mixture increased significantly at each shrinkage height. Measuring the melting properties of sintering raw materials with different MgO contents revealed that the sintering raw materials with a high MgO content could inhibit the formation of the low-temperature liquid phase. The experimental results were consistent with the calculation results obtained using FactSage 7.1.
3.3. Effect of Al2O3 Content on Liquid Amount of Sinter
The liquid amount of the sinter with different Al
2O
3 contents was calculated using the FactSage 7.1. The Al
2O
3 contents in the sintering raw material increased from 1.5% to 2.1% in Groups 1, 8, and 9 of the experimental scheme, which revealed the effect of the Al
2O
3 content on the liquid amount of the sinter. The calculation results are shown in
Figure 9.
As shown in
Figure 9, with an increase in the Al
2O
3 content in the sintering material, the liquid region of the system moved toward the CaO-SiO
2 line. When the Al
2O
3 content increased to 1.8%, the liquid region of the CaO-SiO
2-FeOx-Al
2O
3-MgO system at a low temperature expanded, and that at a high temperature shrank. When the Al
2O
3 content increased to 2.1%, the liquid phase region near the CaO-Fe
2O
3 line expanded, but it shrank near isobaric line a and disappeared at a low temperature (<1350 °C). Line a is the isobaric line of 1.9, and point A is the corresponding point of the sintering material. Point C (D and E) is the intersection point of the isobaric line and liquid line. The liquid amount of the sinter with different Al
2O
3 contents was compared using the phase diagram lever principle. With an increase in the Al
2O
3 content, the length of AB remained essentially unchanged. When the Al
2O
3 content increased to 1.8%, the length variation of AC (D and E) was not obvious by comparing
Figure 9a,b. When the Al
2O
3 content reached 2.1%, the liquid region of the isobaric line shrank, and the length of line AC increased. Owing to the lever principle, the increase in the Al
2O
3 content from 1.8% to 2.1% inhibited the liquid formation of the sinter.
To precisely determine the effects of the Al
2O
3 content on the mineral composition and liquid phase amount of the sinter, the mineral composition and liquid phase amount were calculated using the Equilibrium module of the FactSage 7.1. The calculation results are shown in
Figure 10.
As shown in
Figure 10, when the Al
2O
3 content increased from 1.5% to 1.8%, the liquid-formation temperature of the sinter did not change to 1137.7 °C, and the liquid amount of the sinter increased at a low temperature but decreased at a high temperature (>1250 °C). When the Al
2O
3 content increased from 1.8% to 2.1%, the liquid phase formation temperature of the sinter increased from 1137.7 to 1145.1 °C, and the liquid phase amount decreased significantly. The calculation results of the Equilibrium module were consistent with those of the Phase Diagram module. An appropriate Al
2O
3 content in the sinter material can promote the formation of the liquid phase; however, excess Al
2O
3 can inhibit the formation of the liquid phase. Therefore, when iron ore is sintered with biomass fuel, the amount of biomass fuel can be increased by adding an appropriate amount of Al
2O
3 to the sintering material.
As indicated by
Figure 11 and
Table 4, two endothermic peaks were observed for the sintering materials with different Al
2O
3 contents at 450 and 1200 °C, corresponding to Ca(OH)
2 decomposition and the calcium ferrite formation phase, respectively. Comparing the peak endothermic temperatures and areas of the sintering raw material with different Al
2O
3 contents at approximately 1200 °C reveals that when the Al
2O
3 content increased to 1.8%, the peak temperature of the calcium ferrite formation phase in the sintering raw material remained essentially unchanged, and the peak area increased slightly. When the Al
2O
3 content increased to 2.1%, the peak area of the sintering material at 1200 °C decreased, indicating a decrease in the amount of the liquid phase. The DSC results were consistent with the FactSage 7.1 calculations. Increasing the Al
2O
3 content in the sintering raw material could increase the amount of the liquid phase; however, an excessive amount of Al
2O
3 was not conducive to the formation of the liquid phase. Therefore, the Al
2O
3 content in the sintering raw material should be adjusted appropriately under the condition of low-temperature sintering.
According to the experimental scheme described in
Table 1, the melting properties of the sintering raw materials were tested using a high-temperature melting property tester. The melting property can reflect the influence of the Al
2O
3 content on the liquid phase formation ability of a sintered mixture. Additionally, the simulation results were verified.
As shown in
Figure 12, when the Al
2O
3 content in the sintering raw materials increased from 1.5% to 1.8%, the T10% decreased, indicating that the increase in the Al
2O
3 content reduced the initial melting temperature of the sintering raw material. When the Al
2O
3 content in the sintering materials increased to 2.1%, the shrinkage temperature increased significantly. Measuring the melting properties of sintering raw materials with different Al
2O
3 contents at a high temperature revealed that a certain amount of Al
2O
3 promoted the melting of the sintering raw materials at a low temperature, but excessive Al
2O
3 inhibited the melting of the sintering raw materials. The experimental results differed slightly from the calculation results obtained using FactSage 7.1 for an Al
2O
3 content of 1.8% in the sintering raw materials. Thermodynamic calculations indicated that the liquid phase formation of the raw material with an Al
2O
3 content of 1.8% was greater than that of the raw material with an Al
2O
3 content of 1.5% only when the temperature was below 1250 °C. However, the melting properties of the raw materials with an Al
2O
3 content of 1.8% were poorer than those of the raw materials with an Al
2O
3 content of 1.5% under all the shrinkage rates. This may be due to the strong liquid phase formation ability and low viscosity of the raw material with 1.8% Al
2O
3 at a low temperature, which caused a continuous reduction in the shrinkage temperature owing to the rapid shrinkage in the melting property experiment. Although there was a gap between the results of the thermodynamic calculations and the melting-property experiment, the accuracy of the FactSage 7.1 calculation for predicting the liquid phase formation ability was verified.