Research on the Preparation and Properties of High Belite Sulphoaluminate Cement (HBSAC) Based on Various Industrial Solid Wastes

In this study, a variety of industrial solid wastes, including petroleum coke desulfurization slag, fly ash and carbide slag with natural resource bauxite, were used as raw materials to prepare high belite suphoaluminate cement, which contains a certain CaSO4 content without adding natural gypsum to the clinker. The sintering temperature, mineral composition, and the physical and mechanical properties of the cement clinkers were investigated. The techniques adopted included a comprehensive thermal analysis (DSC-TG), X-ray diffraction (XRD), X-ray fluorescence (XRF) and scanning electron microscopy (SEM). The results revealed that it is completely feasible to prepare high belite sulphoaluminate cement with the various industrial solid wastes mentioned above and the utilization rate of the solid wastes is up to 80%. The sintering temperature ranges from 1225 °C to 1350 °C, and the optimal sintering temperature is approximately 1300 °C. The clinkers prepared at 1300 °C set and harden quickly and have a slightly higher water requirement of normal consistency. The mechanical strength is greatly affected by the CaSO4 and 3CaO·3Al2O3·CaSO4 contents and the most reasonable CaSO4 content is 15%.


Introduction
Sulphoaluminate cement (SAC) is the third series of cements after Portland cement and aluminate cement, and it has the characteristics of early strength, high strength, high impermeability, high frost resistance, corrosion resistance, low alkali and low production energy consumption; SAC is widely used in rapid construction, rapid repair, winter construction, marine environments and underground engineering [1][2][3]. Its clinker is mainly composed of C 4 A 3 S (ye'elimite, 3CaO·3Al 2 O 3 ·CaSO 4 ) and β-C 2 S (belite, 2CaO·SiO 2 ). Among them, C 4 A 3 S is an early strength mineral that can quickly hydrate to AFt (ettringite, 3CaO·Al 2 O 3 ·3CaSO 4 ·32H 2 O) in the presence of gypsum to provide early strength [4]. Compared with C 3 S (alite, 3CaO·SiO 2 ), the main mineral component of Portland cement, the formation temperature of C 4 A 3 S and the content of CaO are lower [5]. It not only saves a great deal of coal, power and limestone resources but also reduces CO 2 emissions [6]. However, SAC has many defects, such as the low content and slow hydration of C 2 S, resulting in no significant increase in the later strength of SAC [7,8]; the formation of C 4 A 3 S requires a large amount of natural gypsum and high-quality aluminum resources.

Mix Design
In the process of developing a mixing design, it is assumed that the mineral formation reactions proceed as follows: (1)4CaO + Al 2 O 3 + Fe 2 O 3 →C 4 AF (tetracalcium aluminoferrite, 4CaO·Al 2 O 3 ·Fe 2 O 3 ); (2)3CaO + 3Al 2 O 3 + CS→C 4 A 3 S; (3)2CaO + SiO 2 →β-C 2 S. Then, the mineral content of the target clinker should be set. In this study, a total of nine ratios in three series were designed, as shown in Table 2. Based on the mineral composition of the clinker, the chemical composition of the clinker can be calculated, and then the amounts of raw materials can be deduced. Meanwhile, it is necessary to control the alkalinity coefficient of the clinkers (i.e., C m ) [1] so that it is not less than 1.0, as it will also affect the raw material amounts, especially for the calcareous materials.

Preparation of Clinkers
The preparation of clinkers by using various industrial solid wastes can be divided into three steps: grinding and molding, preheating and sintering, and cooling and regrinding. The specific operations are as follows: (1) All of the raw materials were ground by a cement mill to pass through a 200 mesh square hole sieve and then mixed evenly and pressed into a steel matrix to form cylindrical test samples with a diameter of 15 mm and a height of 17 mm. (2) Samples were dried for 1 h in a drying oven at a constant temperature of 105 ± 5 • C and then preheated for 30 min in a high temperature electric furnace (SX-8-16 type, Beijing Ever Bright Medical Treatment Instruments Co., Ltd., Beijing, China) at a constant temperature of 950 • C and then sintered for 30 min in another high temperature electric furnace at a constant temperature. (3) The samples were removed and air cooled [24] and then ground to pass through a 200-mesh square hole sieve with a surplus of less than 5% or a Boer's specific surface area of approximately 400 kg/m 3 . The processing diagram is shown in Figure 1.

Preparation of Clinkers
The preparation of clinkers by using various industrial solid wastes can be divided into three steps: grinding and molding, preheating and sintering, and cooling and regrinding. The specific operations are as follows: (1) All of the raw materials were ground by a cement mill to pass through a 200 mesh square hole sieve and then mixed evenly and pressed into a steel matrix to form cylindrical test samples with a diameter of 15 mm and a height of 17 mm. (2) Samples were dried for 1 hour in a drying oven at a constant temperature of 105 ± 5 °C and then preheated for 30 minutes in a high temperature electric furnace (SX-8-16 type, Beijing Ever Bright Medical Treatment Instruments Co., Ltd., Beijing, China) at a constant temperature of 950 °C and then sintered for 30 minutes in another high temperature electric furnace at a constant temperature. (3) The samples were removed and air cooled [24] and then ground to pass through a 200-mesh square hole sieve with a surplus of less than 5% or a Boer's specific surface area of approximately 400 kg/m 3 . The processing diagram is shown in Figure 1.

Test Methods
A comprehensive thermal analyzer (SDT Q600 type, TA Instruments Co., New Castle, DE, U.S.A.) was employed to measure the weight change, the heat absorption and exothermy of raw materials during the sintering process, while the weight was monitored from room temperature (approximately 20 °C) to 1400 °C at a heating rate of 20 °C/min while continuously purging with N2.
The mineral phase and hydration products of the clinkers were detected by an X-ray diffraction instrument (D8 advance type, Bruker Co., Karlsruhe, Germany) with the working conditions as follows: Cu target, voltage at 40 kV, current at 40 mA, 2-Theta scanning ranges from 5-60°, step width of 0.02° and a residence time of 0.05 s. The main chemical composition of the clinkers were measured by an X-ray fluorescence spectrometry (1800 type, Shimadzu Co., Kyoto, Japan). The basic physical properties of the clinkers, such as the water consumption at standard consistency and setting time, were determined according to the "Test methods for water requirement of normal consistency, setting time and soundness of the portland cement" (GB/T 1346-2011, China). According to the "Method of testing cements-Determination of strength" (GB/T 17671-1999, China)

Test Methods
A comprehensive thermal analyzer (SDT Q600 type, TA Instruments Co., New Castle, DE, U.S.A.) was employed to measure the weight change, the heat absorption and exothermy of raw materials during the sintering process, while the weight was monitored from room temperature (approximately 20 • C) to 1400 • C at a heating rate of 20 • C/min while continuously purging with N 2 . The mineral phase and hydration products of the clinkers were detected by an X-ray diffraction instrument (D8 advance type, Bruker Co., Karlsruhe, Germany) with the working conditions as follows: Cu target, voltage at 40 kV, current at 40 mA, 2-Theta scanning ranges from 5-60 • , step width of 0.02 • and a residence time of 0.05 s. The main chemical composition of the clinkers were measured by an X-ray fluorescence spectrometry (1800 type, Shimadzu Co., Kyoto, Japan). The basic physical properties of the clinkers, such as the water consumption at standard consistency and setting time, were determined according to the "Test methods for water requirement of normal consistency, setting time and soundness of the portland cement" (GB/T 1346-2011, China). According to the "Method of testing cements-Determination of strength" (GB/T 17671-1999, China) and the "Sulphoaluminate cement" (GB 20472-2006, China), the mechanical strength was tested, and the cement mortar pieces used were 40 × 40 × 160 mm samples prepared under a water-cement ratio of 0.52, which were cured for 1, 3, 7 and 28 days, respectively. A scanning electron microscope (JSM-7500F type, JEOL Co., LTD., Tokyo, Japan) with a working voltage of 5.0 kV was used to analyze the micromorphology of the clinker minerals and hydration products. The clinker samples were powdered, and the samples of the hydration products used were small pieces, which were sprayed with gold before testing.

Sintering Temperature of Clinkers
Comprehensive thermal analysis can characterize the mass and heat changes in the clinker formation process to approximate preliminarily the temperature of the reaction among the raw materials. As shown in Figure 2, the DSC-TG curves of the mixtures (i.e., samples I-1, II-1 and III-1) show a similar change rule. Combined with the DSC-TG curves of the raw materials in Figure 3, it is not difficult to obtain some meaningful results: when the temperature is below 200 • C, the endothermic peaks and mass loss in the DSC-TG curves should originate from the evaporation of the physical water in all the raw materials; when temperature reaches 400-500 • C, an endothermic peak should be caused by the decomposition of the Ca(OH) 2 in the petroleum coke desulfurization slag (formed by the CaO absorbing water from the air) and in the carbide slag; at approximately 710 • C, 910 • C and 1050 • C, there are different sized endothermic peaks with mass loss, which are still caused by the petroleum coke desulfurization slag and carbide slag. It appears that there was no new mineral formation before 1050 • C, and in this process, the mass loss and heat change of the fly ash and bauxite were also not significant. The reason may be that these two raw materials have excellent resistance to elevated temperatures. After 1050 • C, all the raw materials were involved in the reaction, including a series of chemical changes such as the decomposition of the CS, the formation and decomposition of the C 2 AS (gehlenite, 2CaO·Al 2 O 3 ·SiO 2 ) [21], C 4 A 3 S, C 5 S 2 S (ternesite, 4CaO·2SiO 2 ·CaSO 4 ) [21,25,26] and β-C 2 S. The comprehensive effect was to form exothermic peaks in the 1050-1350 • C range, which was also used preliminarily as the sintering temperature. , the mechanical strength was tested, and the cement mortar pieces used were 40 × 40 × 160 mm samples prepared under a water-cement ratio of 0.52, which were cured for 1, 3, 7 and 28 days, respectively. A scanning electron microscope (JSM-7500F type, JEOL Co., LTD., Tokyo, Japan) with a working voltage of 5.0 kV was used to analyze the micromorphology of the clinker minerals and hydration products. The clinker samples were powdered, and the samples of the hydration products used were small pieces, which were sprayed with gold before testing.

Sintering Temperature of Clinkers
Comprehensive thermal analysis can characterize the mass and heat changes in the clinker formation process to approximate preliminarily the temperature of the reaction among the raw materials. As shown in Figure 2, the DSC-TG curves of the mixtures (i.e., samples I-1, II-1 and III-1) show a similar change rule. Combined with the DSC-TG curves of the raw materials in Figure 3, it is not difficult to obtain some meaningful results: when the temperature is below 200 °C, the endothermic peaks and mass loss in the DSC-TG curves should originate from the evaporation of the physical water in all the raw materials; when temperature reaches 400-500 °C, an endothermic peak should be caused by the decomposition of the Ca(OH)2 in the petroleum coke desulfurization slag (formed by the CaO absorbing water from the air) and in the carbide slag; at approximately 710 °C, 910 °C and 1050 °C, there are different sized endothermic peaks with mass loss, which are still caused by the petroleum coke desulfurization slag and carbide slag. It appears that there was no new mineral formation before 1050 °C, and in this process, the mass loss and heat change of the fly ash and bauxite were also not significant. The reason may be that these two raw materials have excellent resistance to elevated temperatures. After 1050 °C, all the raw materials were involved in the reaction, including a series of chemical changes such as the decomposition of the CS -, the formation and decomposition of the C2AS (gehlenite, 2CaO·Al2O3·SiO2) [21], C4A3S -, C5S2S -(ternesite, 4CaO·2SiO2·CaSO4) [21,25,26] and β-C2S. The comprehensive effect was to form exothermic peaks in the 1050-1350°C range, which was also used preliminarily as the sintering temperature.
(a) To determine the clinker sintering temperature and assess the formation of products more accurately, an X-ray diffraction analysis was carried out. The X-ray diffraction (XRD) patterns of the sampleII-1 cement clinker at different temperaturesare given in Figure 4. When the sintering temperature is in the range of 950-1100 • C, the main products are CS, C 2 AS, CaO, Al 2 O 3 and SiO 2 , and C 4 A 3 S begins to form in a small amount at 1050 • C, which is consistent with the results of the comprehensive thermal analysis. The temperature rises to 1150-1225 • C, C 4 A 3 S gradually forms in large quantities; additionally, the C 2 AS disappears and C 5 S 2 S appears, and the sintering products are mainly C 4 A 3 S and C 5 S 2 S. As the temperature continues to rise to 1250-1300 • C, the C 5 S 2 S decomposes, and β-C 2 S gradually forms; the main products are C 4 A 3 S, β-C 2 S and CS. At the same time, the intensity of the C 4 A 3 S and β-C 2 S diffraction peaks increases with the increase in temperature, while that of the CS decreases, indicating that the increase in temperature promotes high temperature reactions. As the temperature increases again, the intensity of the diffraction peaks of each product begins to decrease, and the CS diffraction peaks are hardly observed, especially after 1350 • C. This finding indicates that the increase in temperature has caused the decomposition of the mineral phases. It can be seen that the sintering temperature of the sample II-1 cement clinker ranges from 1250 • C to 1350 • C, and the optimum sintering temperature is 1300 • C. It is worth pointing out that the iron element did not form the anticipated C 4 AF but mainly formed C 4   To determine the clinker sintering temperature and assess the formation of products more accurately, an X-ray diffraction analysis was carried out. The X-ray diffraction (XRD) patterns of the sample II-1 cement clinker at different temperatures are given in Figure 4. When the sintering temperature is in the range of 950-1100 °C, the main products are CS -, C2AS, CaO, Al2O3 and SiO2, and C4A3S begins to form in a small amount at 1050 °C, which is consistent with the results of the comprehensive thermal analysis. The temperature rises to 1150-1225 °C, C4A3S gradually forms in large quantities; additionally, the C2AS disappears and C5S2S appears, and the sintering products are mainly C4A3S and C5S2S -. As the temperature continues to rise to 1250-1300 °C, the C5S2S decomposes, and β-C2S gradually forms; the main products are C4A3S -, β-C2S and CS -. At the same time, the intensity of the C4A3 S and β-C2S diffraction peaks increases with the increase in temperature, while that of the CS decreases, indicating that the increase in temperature promotes high temperature reactions. As the temperature increases again, the intensity of the diffraction peaks of each product begins to decrease, and the CS diffraction peaks are hardly observed, especially after 1350 °C. This finding indicates that the increase in temperature has caused the decomposition of the mineral phases. It can be seen that the sintering temperature of the sample II-1 cement clinker ranges from 1250 °C to 1350 °C, and the optimum sintering temperature is 1300 °C.
It is worth pointing out that the iron element did not form the anticipated C4AF but mainly formed C4A2.85Fe1.5S -(3CaO·2.85Al2O3·1.5Fe2O3·CaSO4) by solid solution in the C4A3S - [25], regardless of the sintering temperature.  In accordance with the same principle of analysis, all the other mix proportions besides sample II-1 were tested to study the influence of the mix proportion on the sintering temperature. Some of the results are shown in Figures 5-7. As revealed in these figures, the sintering temperature ranges of the Series I, II, and III cement clinkers are approximately 1225-1325 • C,1250-1350 • C, and 1275-1350 • C, respectively. Thus, with the increase of the CS content in the mix design, the lower limit of the sintering temperature increases gradually, which is controlled by the decomposition of C 5 S 2 S, and the range of the sintering temperature is basically maintained at 100 • C. In addition, the optimal sintering temperature of all the mix proportions is approximately 1300 • C. 1350 °C, respectively. Thus, with the increase of the CS content in the mix design, the lower limit of the sintering temperature increases gradually, which is controlled by the decomposition of C5S2S -, and the range of the sintering temperature is basically maintained at 100 °C. In addition, the optimal sintering temperature of all the mix proportions is approximately 1300 °C.    1350 °C, respectively. Thus, with the increase of the CS content in the mix design, the lower limit of the sintering temperature increases gradually, which is controlled by the decomposition of C5S2S -, and the range of the sintering temperature is basically maintained at 100 °C. In addition, the optimal sintering temperature of all the mix proportions is approximately 1300 °C.

Mineral Composition of Clinkers
The micromorphology of the minerals in the clinker was observed by scanning electron microscopy (SEM), and the mineral composition was qualitatively analyzed. Taking the sample II-1 cement clinker prepared at 1300 °C as an example, the results are shown in Figure 8. The cement clinker system was mainly composed of tabular C4A3S -, blocky granular β-C2S, and radical and needle-bar CS -. The mineral composition is basically consistent with the X-ray diffraction analysis. In addition to the qualitative analysis of the mineral composition, a quantitative analysis of the clinker minerals was also carried out. The chemical composition of the cement clinkers prepared at 1300 °C was measured as shown in Table 3. The clinker mineral content is calculated according to Bogue's equation [27]. However, because of the existence of residual CS and C4A2.85Fe1.5S and the absence of C4AF in the cement clinker, Bogue's equation needs to be modified [28][29][30][31], as shown in Equations (1)-(4), while the alkalinity coefficient is also been modified, as shown in Equation (5).

Mineral Composition of Clinkers
The micromorphology of the minerals in the clinker was observed by scanning electron microscopy (SEM), and the mineral composition was qualitatively analyzed. Taking the sample II-1 cement clinker prepared at 1300 • C as an example, the results are shown in Figure 8. The cement clinker system was mainly composed of tabular C 4 A 3 S, blocky granular β-C 2 S, and radical and needle-bar CS. The mineral composition is basically consistent with the X-ray diffraction analysis.

Mineral Composition of Clinkers
The micromorphology of the minerals in the clinker was observed by scanning electron microscopy (SEM), and the mineral composition was qualitatively analyzed. Taking the sample II-1 cement clinker prepared at 1300 °C as an example, the results are shown in Figure 8. The cement clinker system was mainly composed of tabular C4A3S -, blocky granular β-C2S, and radical and needle-bar CS -. The mineral composition is basically consistent with the X-ray diffraction analysis. In addition to the qualitative analysis of the mineral composition, a quantitative analysis of the clinker minerals was also carried out. The chemical composition of the cement clinkers prepared at 1300 °C was measured as shown in Table 3. The clinker mineral content is calculated according to Bogue's equation [27]. However, because of the existence of residual CS and C4A2.85Fe1.5S and the absence of C4AF in the cement clinker, Bogue's equation needs to be modified [28][29][30][31], as shown in Equations (1)-(4), while the alkalinity coefficient is also been modified, as shown in Equation (5). In addition to the qualitative analysis of the mineral composition, a quantitative analysis of the clinker minerals was also carried out. The chemical composition of the cement clinkers prepared at 1300 • C was measured as shown in Table 3. The clinker mineral content is calculated according to Bogue's equation [27]. However, because of the existence of residual CS and C 4 A 2.85 Fe 1.5 S and the absence of C 4 AF in the cement clinker, Bogue's equation needs to be modified [28][29][30][31], as shown in Equations (1)-(4), while the alkalinity coefficient is also been modified, as shown in Equation (5).  As revealed in Table 4, the actual mineral content of the cement clinker is not significantly different from the design content in Table 2. More specifically, the content error of the C 4 A 3 S and β-C 2 S is approximately 5%, while that of the CS is within 2%, even the content error between the C 4 A 2.85 Fe 1.5 S and C 4 AF is less than 5%. In addition, the alkalinity coefficients of all the clinkers are slightly greater than 1.0, indicating that the CaO in the raw materials can meet the requirements for the formation of various useful minerals. By the qualitative and quantitative analyses mentioned above, the mineral composition of the clinkers basically conforms to the expected product, and it is indirectly proven that the mix design and sintering conditions are reasonable.

Physical and Mechanical Properties of the Clinkers
The physical and mechanical properties are the most basic elements of cement performance. In this study, the water requirement of normal consistency, setting time and mechanical strength of the clinkers with different proportions prepared at 1300 • C were tested. As shown in Table 5, the water requirement of normal consistency, which was prepared by using various solid wastes, is in the range of 36%-40%, which is slightly larger than that of typical clinkers (approximately 30%). The initial setting time and the final setting time are 17-25 min and 23-40 min, respectively. The setting time is relatively short, which is more suitable for projects involving emergency rescue and repair. Further analysis shows that the water requirement of normal consistency decreases and the setting time prolongs as the C 4 A 3 S content decreases in each series. In view of the fact that the early hydration of HBSAC is dominated by C 4 A 3 S [32][33][34], it can be considered that the C 4 A 3 S content plays a direct and decisive role in the water requirement of normal consistency and in the setting time . Comparing sample I-1 with  II-1, or sample I-2, II-2 with III-1, or sample I-3 with III-2, it is easy to find that the water requirement of normal consistency decreases and the setting time shortens as the CS content increases under the same C 4 A 3 S content, which indicates that an increase in the CS content in the range of 10%-20% helps to accelerate the C 4 A 3 S hydration.  Figure 9 shows the mechanical strength of the cement clinkers measured by using the mortar pieces at a water-cement ratio of 0.52. As shown in Figure 9a, the bending strength of each series increases as the curing age increases, and the bending strength increases rapidly within 3 days and slows down after 3 days. For example, as the lowest early bending strengths of all the mixtures, the bending strengths of sample I-3 at 1, 3, 7 and 28 days are 2.4 MPa, 3.8 MPa, 5.2 MPa and 6.2 MPa, respectively, while the strength increases at 3, 7 and 28 days are 58%, 37% and 20%, respectively. Sample II-2, as the middle early bending strength sample of all the mixtures, has bending strengths of 5.5 MPa, 6.1 MPa, 6.2 MPa and 6.4 MPa, respectively at 1, 3, 7 and 28 days, and strength increases of 11%, 2% and 3%, respectively at 3, 7 and 28 days. Of all the mixtures, sample III-1 has the highest early bending strength; its bending strengths at 1, 3, 7 and 28 days are 6.0 MPa, 6.3 MPa, 6.6 MPa and 6.8 MPa, respectively, while the strength increases at 3, 7 and 28 days are 5%, 5%, and 3%, respectively. In addition, there are several other findings: (1) The increase in the bending strength of the samples in Series II and III at 7 days has decreased to less than 5%, while that of the samples in Series I is approximately 30%, which indicates that the increased CS content in the clinker has an obvious positive effect on the development of early bending strength [35]. (2) Comparing the bending strength of samples I-1 and II-1 (or samples I-2, II-2 and III-1) at different curing ages, it can be seen that under the same C 4 A 3 S content, the bending strength at 1, 3, and 7 days increases as the CS content increases. However, there is no similar trend for the bending strength at 28 days, which shows from another perspective that the increased CS content in the clinker has an obvious positive effect on the development of early bending strength. The bending strength at 28 days decreases with the β-C 2 S content decreases, which means that the hydration of β-C 2 S is the main factor for the strength development of the cement clinker in the later stage [36]. (3) During the entire 28-day curing process, the bending strength of each series decreases as the C 4 A 3 S content decreases. The β-C 2 S content does not change the development trend of the later strength, indicating that the hydration of β-C 2 S in the clinker is not so strong that the bending strength of the cement clinkers at 28 days is still dominated by the C 4 A 3 S content.  Com pressive strength / M Pa -1 Ⅲ-2 Ⅲ-3 Cu rin g age  In terms of compressive strength, as shown in Figure 9b, there are obvious differences among the three series with the increase in the curing age. The compressive strength of Series I and III samples decreases at 28 days, while that of Series II samples maintains good growth during the whole curing age. It can be seen that the CS content in the clinker is not as high as possible, a lower or higher CS content in the clinker may have a negative impact on the compressive strength. The reasons are as follows: when the CS content is lower, the AFt phase formed in the early hydration stage is partly converted to the AFm (ettringite, C 3 A·CaSO 4 ·12H 2 O) phase in the later hydration stage [37][38][39], as shown in Figure 10, which results in a decrease in the compressive strength; when the CS content is higher, the rate of the AFt phase formation in the early hydration stage is too fast, and the crystal structure continues to grow in the later hydration stage, which causes expansion and microcrack damage [26], and also results in a decrease in the compressive strength. According to the results of this experiment, 15% is the optimal CS content in this kind of cement clinker; under this content, the lowest compressive strengths are 42. The formation of the hydration products can reasonably reflect the development of the cement strength. As shown in Figure 11, the main hydration product of the cement is the AFt phase, and the C4A3S hydration is the main hydration reaction during the 7 days, while CS is gradually consumed. The C2S hydration is slow, and C2S diffraction peaks in the XRD patterns still change slightly at 28 days. In Figure 12, the needle bar phase is the AFt phase, and at the initial hydration stage, the AFt phase are fine needle rods, which gradually develop into thick needle rods as the curing age increases. At the later hydration stage, the flocculent C-S-H gel phase appears and intercalates with the needle AFt phase, which makes the structure of the cement paste denser and further increases the strength. Thus, the formation process of the hydration products coincides with the strength development law as the curing age increases. In addition, the XRD patterns and SEM micromorphology of the hydration products of the Series I cement clinker before 28 days and the Series II cement clinker during the whole curing age, are basically similar to those of the Series II cement clinker and are not listed here. The formation of the hydration products can reasonably reflect the development of the cement strength. As shown in Figure 11, the main hydration product of the cement is the AFt phase, and the C 4 A 3 S hydration is the main hydration reaction during the 7 days, while CS is gradually consumed. The C 2 S hydration is slow, and C 2 S diffraction peaks in the XRD patterns still change slightly at 28 days. In Figure 12, the needle bar phase is the AFt phase, and at the initial hydration stage, the AFt phase are fine needle rods, which gradually develop into thick needle rods as the curing age increases. At the later hydration stage, the flocculent C-S-H gel phase appears and intercalates with the needle AFt phase, which makes the structure of the cement paste denser and further increases the strength. Thus, the formation process of the hydration products coincides with the strength development law as the curing age increases. In addition, the XRD patterns and SEM micromorphology of the hydration products of the Series I cement clinker before 28 days and the Series II cement clinker during the whole curing age, are basically similar to those of the Series II cement clinker and are not listed here. The formation of the hydration products can reasonably reflect the development of the cement strength. As shown in Figure 11, the main hydration product of the cement is the AFt phase, and the C4A3S hydration is the main hydration reaction during the 7 days, while CS is gradually consumed. The C2S hydration is slow, and C2S diffraction peaks in the XRD patterns still change slightly at 28 days. In Figure 12, the needle bar phase is the AFt phase, and at the initial hydration stage, the AFt phase are fine needle rods, which gradually develop into thick needle rods as the curing age increases. At the later hydration stage, the flocculent C-S-H gel phase appears and intercalates with the needle AFt phase, which makes the structure of the cement paste denser and further increases the strength. Thus, the formation process of the hydration products coincides with the strength development law as the curing age increases. In addition, the XRD patterns and SEM micromorphology of the hydration products of the Series I cement clinker before 28 days and the Series II cement clinker during the whole curing age, are basically similar to those of the Series II cement clinker and are not listed here. The formation of the hydration products can reasonably reflect the development of the cement strength. As shown in Figure 11, the main hydration product of the cement is the AFt phase, and the C4A3S hydration is the main hydration reaction during the 7 days, while CS is gradually consumed. The C2S hydration is slow, and C2S diffraction peaks in the XRD patterns still change slightly at 28 days. In Figure 12, the needle bar phase is the AFt phase, and at the initial hydration stage, the AFt phase are fine needle rods, which gradually develop into thick needle rods as the curing age increases. At the later hydration stage, the flocculent C-S-H gel phase appears and intercalates with the needle AFt phase, which makes the structure of the cement paste denser and further increases the strength. Thus, the formation process of the hydration products coincides with the strength development law as the curing age increases. In addition, the XRD patterns and SEM micromorphology of the hydration products of the Series I cement clinker before 28 days and the Series II cement clinker during the whole curing age, are basically similar to those of the Series II cement clinker and are not listed here.

Conclusions
It is completely feasible to prepare HBSAC with petroleum coke desulfurization slag, fly ash, carbide slag and bauxite synergistically. The cement clinkers prepared contain 10%-20% of CS without adding additional natural gypsum. The comprehensive utilization rate of the solid waste is up to 80%.
The sintering temperature range of the cement clinkers prepared with solid wastes such as petroleum coke desulfurization slag and fly ash is 1225-1350 • C, and with a 5% gradient increase in the cement clinker CS content, the lower limit of the sintering temperature increases by a 25 • C gradient, which is caused by the increase in the C 5 S 2 S decomposition temperature. The optimal sintering temperature is approximately 1300 • C.
The mineral composition of the cement clinkers prepared with solid wastes such as petroleum coke desulfurization slag and fly ash is mainly C 4 A 3 S, β-C 2 S and CS. The iron element does not form the anticipated C 4 AF but mainly forms C 4 A 2.85 Fe 1.5 S by solid solution in C 4 A 3 S. The difference between the actual mineral content and the designed mineral content of the clinkers is within a reasonable range.
The cement clinkers prepared at 1300 • C set and harden quickly and have a slightly higher water requirement of normal consistency. The water requirement of normal consistency is 36%-40%, and the initial setting time and final setting time are 17-23 min, 25-40 min, respectively. The mechanical strength is greatly affected by the clinker CS and C 4 A 3 Scontents, and the optimal CS content is 15%. In terms of the hydration products of the cement clinkers, the AFt and C-S-H gel are still the main phases, which are formed by C 4 A 3 S hydration at the early stage and C 2 S hydration at the later stage, respectively.