Experimental Investigation of Different Fineness and Firing Temperatures on Pellets Properties of Different Iron Ore fines from Indian Mines

In India, during mining and ore processing, ore fine generation is a common phenomenon, in which more than 60% of process ore becomes discarded material. To explore the alternative of high-grade ores, mutual replacement with the utility of dump ore fines is the best way. With this perspective, Kiruburu iron ore mine (Iron Ore No.1) and Meghataburu iron ore mine (Iron Ore No.2) dumped fines were chosen for a Blaine no. investigation, in the connection of firing temperatures, to get optimum desirable physical properties, Cold Compression Strength (C.C.S.),and Apparent Porosity (A.P.), with physico-chemical properties, Reducibility Degradation Index (R.D.I.), and Reducibility Index (R.I.). To characterize pellet properties with input variables, a microstructure phase study has been conducted using a scanning electron microscope (S.E.M.), energy dispersive spectroscopy (EDS), and X-ray diffraction analysis (XRD). The Iron Ore No.1 and 2 fine pellets survey showed good, desirable properties, at the Blaine no., of 1678 cm2/g and 2311 cm2/g (corresponding to 200 mesh size), and the best results are attained at a firing temperature of 1300 °C. Thermal kinetic analysis of the heating of pellets has been done to knowthe activation energy of different ore characteristics. The results showed that Iron Ore No.2 pellets have high activation energy.


Introduction
Iron and steel are the most common commodities globally. Its consumption is ever increasing, at a very high rate, in developing countries such as India. The extraction of iron from ore through the blast furnace route is a very common and widely used technique all over the world. The feedstock of the blast furnace mainly contains lump ore, partial pellets, and sinter. Ore particles of various sizes, in a certain range, are suitable for feedstock to enhance the effectiveness of the process. Iron ore availability in India is mainly in the form of hematite, magnetite, and goethite. Mainly, hematite iron ore is found abundantly, and to use iron ore blast furnace feedstock, lump ore preparation is required. During the lump ore preparation, ore dressing generates a significant amount of fines. Washing generates micro fines (less than 30 µm), and approximately 60% of the ore fines are generated.
Along with the fine size, chemical components, such as alumina, cause higher flux consumption and the production of viscous content. Alumina and silica gangue content restricted the utility of iron fines, even when they were bearing enough iron. Moreover, hydroxyl bearing (goethite ore) content has high loss on ignition (LOI) in the iron ore concentrate. Therefore, these fines cannot employ in the furnace without property customization of feedstock, such as sintering and pelletization. Fineness of less than 0.5 mm The microstructural investigation is an informative tool to control pellet quality based on the process parameters. A comparative study has been done on fineness, as well as the drying and heating processes. As per the chemistry of an ore pellet's microstructure, the formation and impact on physical and physicochemical properties were investigated [9,10].

Pellets Making
Iron ore concentrates were collected from Iron ore No.1 and Iron ore No.2, located in India. These ores are of pre-Cambrian origin, but Iron ore No.1 has a hard laminated nature, while Iron ore No.2 ore has a soft laminated nature.After, the concentration of ore is 62.42% Fe, 2.98% SiO 2 , 1.91% Al 2 O 3 , and 3.61% L.O.I. (Loss on Ignition). The chemistry of Iron Ore No.1 ore fines and the63.48% Fe, 3.07% SiO 2 , 2.68% Al 2 O 3 , and 4.52% L.O.I. of Iron Ore No.2 ore fines was observed.

Fines Sample Preparation
This study is focused on ore fineness; therefore, the surface area is the key parameter of granulometry with the size and shape of particles. Thus, fines' concentrated ground, for obtaining four levels of Blaine fineness, corresponds to four mesh (100, 200, 300 and 400) fineness.
Particle orientation leads to a variety of crystalline phase formations. Blaine fineness of ores was prepared, and their particle size analysis is done [11].

. Green Pellets Preparation
The alkalinity of pellets is a desirable feature, and the addition of the alkaline compound is more advantageous in improving mechanical and metallurgical properties [12]. To encounter the acidic gangue (SiO 2 % + Al 2 O 3 %) content in Iron Ore No.1 and No.2 fines, flux hasbeen added to the ore fines. The raw material mix was composed of coke (−0.074 mm, 1% by weight); dolomite flux (−0.021 mm) to fix basicity 0.6; bentonite (−75 µm, 0.5% by weight) as a binder. Both ores were prepared with the same additives and binder in the same proportion of inclusion. Green pellets were prepared with an average size ranging from 8 to 16 mm.

Pellets Heat Hardening Thermal Treatment Cycle
The thermal treatment has great importance regarding pellet quality. Moreover, additive flux and binders become reactive during heat application and render the pellet's structural strength. Heat hardenings of green samples were carried out in a raising hearth furnace (RHF), as shown in Figure 1. The furnace is equipped with a single chamber and electrical element, with a maximum loading capacity up to 5 Kg samples at one time in a ceramic cylindrical jar.

Thermal Treatment Cycle
The thermal treatment has great importan ditive flux and binders become reactive durin structural strength. Heat hardenings of green s furnace (RHF), as shown in Figure 1. The furn electrical element, with a maximum loading ca ceramic cylindrical jar. The process of pellet heating bifurcates in let samples are tabulated in Table 3.  Drying of pellets occurredin the temperat held at 350 °C for 30 min.  Preheating or intensive drying of pellets h 1000 °C, within 110 min, and held at 1000  The firing of pellets took place at three dif lets. The process of pellet heating bifurcates in three successive stages. Final prepared pellet samples are tabulated in Table 3.
Drying of pellets occurredin the temperature range of 27-350 • C, within 80 min, and held at 350 • C for 30 min. Preheating or intensive drying of pellets happened in the temperature range of 350-1000 • C, within 110 min, and held at 1000 • C for 20 min. The firing of pellets took place at three different temperatures to make 12 sets of pellets.

1.
A-set firing was done from 1000 to 1250 • C, within 80 min, and soaking time was 20 min. 2.
B-set firing was done from 1000 to 1300 • C, within 80 min, and soaking time was 20 min. 3.
C-set firing was done from 1000 to 1350 • C, within 80 min, and soaking time was 20 min. After firing, the fired pellets (of 8 mm to 16 mm) were collected from the furnace. The weight of pellets was noted as 1.221 g to 5.576 g, as per the size range of 8 mm to 16 mm, and an average size of 10 mm pellet weights were observed as 2.898 g.

Physical and Metallurgical Examination of Pellets
The heat-hardened pellets have been examined for their physical properties: cold compression strength (C.C.S.), and Apparent Porosity (A.P.). The compressive strength of indurated pellets has been measured using Aimil's Materials Testing Machine, conforming to the Bureau of Indian Standards (IS 8625-1986) [13]. Apparent Porosity (A.P.) of indurated pellets was measured in a kerosene medium, as per the Bureau of Indian Standards (IS 1528) [14]. The prepared pellets for microstructural analysis were mounted in a cold setting compound. The grinding of sets of the sample was done with sandpaper of 220 µm, 400 µm, 600 µm, 800 µm, 1000 µm, and 1200 µm, and they were polished with a 9 µm diamond suspension solution.
2.4. Reduction DEGRADATION Index (R.D.I.) and Reducibility Index (R.I.) The reducibility index was performed, as per JIS M 8713-2000 (Japanese standard), in the 30% CO and 70% N 2 gas environment, for three hours, at 900 • C. R.D.I. of selected pellets was tested as per JISM8720-2001 (Japanese standard). The average value of each property was taken for analysis [15,16].

Field Emission Scanning Electron Microscopy (F.E.S.E.M.) and Energy Dispersive Spectroscopy (EDS) Analysis
Field Emission Scanning Electron Microscopy (FE-SEM) was conducted for prepared sample pellets with Nova Nano SEM 450 (F.E.I. Company). During Imaging, the chamber pressure was maintained up to −200 Pa and emission current was 99 µA. Image analysis is used to elaborate the information related to phases in the microstructure [17]. EDS was done with X Flash 6130 (Bruker Company). The image analysis tool (ImageJ) was used to measure the area fraction and phase density of different phases in the microstructure [9].

X-ray Diffraction (XRD)
XRD analysis was carried out by Smart Lab 3 kW (Rigaku)-an Automated X-ray Diffractometer-for the phase determination. Fired pellet powder of (−100 mesh) was employed. Radiation Cu-K/opted and 2θ ranges vary from 0 to π/2 during the observation.
Phases identification was carried out by X'Pert HighScore Plus software, R.A.W. files were taken, and background treatment was initiated. Afterward, peaks were searched with 10 minimum significance. Peaks' search and match were done based on KN/pellet own elements. As per the feasibility, score patterns were selected, and patterns of peaks were determined.
Through converting patterns into phases, determined peaks were quantified. To ensure the given quantification, (expanded Rietveld) refinement was done. After refinement, a better phase percentage was obtained [18].

Fourier Transformation Infrared Spectrum (FTIR)
The FT-IR spectra were recorded in Perkin Etmer, Model Spectrum 2; the data range was 400 cm −1 to 4000 cm −1 with diamond crystal. The total number of scans was eight, at a pressure 3 to 4 tons, with a KBr binder on the pellet die that is 12 mm in size. FTIR technique assists to observe the iron ore pellet's behavior in the context of ore fineness and thermal parameters. This analysis shows how the elements are chemically bonded and transformed under a thermal environment, which directly governs the physical and metallurgical properties of pellets by hydroxyl triplet bonding, single bonding, aluminosilicate, loose water, etc. [10].

Fourier Transformation Infrared Spectrum (FTIR)
The FT-IR spectra were recorded in Perkin Etmer, Model Spectrum 2; the data range was 400 cm -1 to 4000 cm -1 with diamond crystal. The total number of scans was eight, at a pressure 3 to 4 tons, with a KBr binder on the pellet die that is 12 mm in size. FTIR technique assists to observe the iron ore pellet's behavior in the context of ore fineness and thermal parameters. This analysis shows how the elements are chemically bonded and transformed under a thermal environment,which directly governs the physical and metallurgical properties of pellets by hydroxyl triplet bonding, single bonding, alumino-silicate, loose water, etc. [10].   G.C.S.: Maximum G.C.S. has been observed at 3.2 kg/pellet for Iron Ore No.1-2425 cm 2 /g pellets and 2.6 kg/pellet for Iron ore No.2-2311 cm 2 /g pellets. Both types of pellets contain <65% of the finer size of −45 µm grains in the pellets. Pellets (Iron Ore No.1-3218 cm 2 /g and Iron ore No.2-2879-3461 cm 2 /g) are having >65% of finer particle proportion, reflecting lower G.C.S. due to the increasing effect of molecular forces resisting the relative mobilization of grains, or it may be due to improper particle arrangement. Finer particles carry moisture in saturation, and this extra moisture may be soaked by dry fines that will be added during pelletizing. This time requires mass transfer through capillaries to get proper green strength [19]. D.C.S.: As the graph reveals that D.C.S. of Iron Ore No.1 pellets increases from 2.1-2.8 kg/pellet, corresponding to 1312-2425 cm 2 /g, Blaine, afterward, decreases to 2 kg/pellet. While iron ore No.2 pellets show growth in D.C.S., from 1989-2311 cm 2 /g, afterward, it reduces from 2.4 to 2.1 kg/pellet. For certain fineness, pellet deterioration occurs, due to the nature of packing. The packing of grains with a gel formation is satisfactory up to an optimum degree of fineness. Afterward, it deteriorates the structure.

Green Pellets Characterization
Drop no strength (D.N.S.) of pellets shows the plasticity by which pellets can sustain an impact. D.N.S. is increased with fineness, as in Figure 2 for Iron Ore No.1 and Iron Ore No.2, respectively. This is because cohesive capillary forces in the pellet pore increase with finer contents of concentrate and assist in plasticity as well.
Moisture: Moisture continuously increases for both types of ore's pellets with increasing fineness of ores. This imparts high plasticity, and it also contrutes to the G.C.S./D.C.S. of pellets. This is observed that, up to a certain percentage of moisture, exhibit property well. After a certain percentage of moisture, the degrading of pelletsis initiated. In the present study, an optimumvalue of 7.4% and 8% of the moisture was found for Iron Ore No.1 and 2 pellets, respectively. The lower moisture than this value results in air inclusion and the loss of capillary effects. That results in a lowering of G.C.S. Above this level, extra water covering the surface of pellets nullifies the capillaries' forces that are reducing G.C.S. Even in dry pellets, a lower level of moisture affects the bonding of the particles and reduces dry strength. Above the optimum level, pellets are left more porous and weakened [10]. S. values are in the acceptable range well, which is above the 2.5 KN/pellet. Since both of the mines' ores are rich in hematite, they require high heat energy for the sintering mechanism during heating. Hematite grains remain less active, up to 1200 • C, resulting in negligible elongation in hematite grains and elimination of defects in the lattice. Up to 1250 • C, initial bridging, crystal growth, and recrystallization commence from the surface shell to the core of pellets [20]. A further mechanism of sintering and oxide bridging succeeded in the presence of coke. On combustion at low temperature, by releasing CO/CO 2 , hematite reduction to magnetite occurs [21]. Since iron ore No.1 and 2 pellets both are hematite ore, hematite begins to react above 1280 • C, while initial crystal formation promotes the strength. Calcium silicate starts to melt and form liquid silicate of calcium ferrite (SCF) at 1250 • C. Al 2 O 3 prone area SCF reacts with and forms SCFA, which is stable at 1300 • C, and liquid phase calcium silicate and iron silicate slag phase are remaining. Firing at 1300 • C initiates the crystal bridging and recrystallization. Secondary hematite starts to sinter by grain growth in the presence of the slag phase, which enhances the process due to ion migration. The hematite reduction phenomenon produces secondary magnetite (secondary hematite), which contributes to forming slag/silicate melt to promote diffusion bonding [22][23][24]. Hence, the strength of pellets is enhanced. Owing to this behavior, pellets roasted at 1300 • C exhibit a higher C.C.S. value, as compared to pellets fired at other firing temperatures of both Iron Ore No.1 and 2 pellets of respective Blaine fineness (1312-1678-2425-3218 cm 2 /g of Iron Ore No.1 and 2311-2879-3461 cm 2 /g of Iron Ore No.2), as shown in Figure 3. Since iron ore No.1 and 2 pellets both are hematite ore, hematite begins to react above 1280 °C, while initial crystal formation promotes the strength. Calcium silicate starts to melt and form liquid silicate of calcium ferrite (SCF) at 1250 °C. Al2O3 prone area SCF reacts with and forms SCFA, which is stable at 1300 °C, and liquid phase calcium silicate and iron silicate slag phase are remaining. Firing at 1300 °C initiates the crystal bridging and recrystallization. Secondary hematite starts to sinter by grain growth in the presence of the slag phase, which enhances the process due to ion migration. The hematite reduction phenomenon produces secondary magnetite (secondary hematite), which contributes to forming slag/silicate melt to promote diffusion bonding [22][23][24]. Hence, the strength of pellets is enhanced. Owing to this behavior, pellets roasted at 1300 °C exhibit a higher C.C.S. value, as compared to pellets fired at other firing temperatures of both Iron Ore No.1 and 2 pellets of respective Blaine fineness (1312-1678-2425-3218 cm 2 /g of Iron Ore No.1 and 2311-2879-3461 cm 2 /g of Iron Ore No.2), as shown in Figure 3.

Fired Pellets Characterization
The lowest C.C.S. is obtained at firing temperature 1350 °C, for both Iron Ore No.1 and 2 pellets, at their respective Blaine fineness (1312-1678-2425-3218 cm 2 /g of Iron Ore No.1 and 2311-2879-3461 cm 2 /g of Iron Ore No.2). Due to increased temperature, high slag/silicate melt formation weakened the pellet structure. Beyond 1350 °C, the temperature of firing hematite dissociation into magnetite and oxygen weakened the strength. The dissociation temperature is decreased with impurities, such as SiO2, CaO, and MgO, dissociation of hematite occurs earlier [22]. While firing above 1200 °C, unreacted magnetite core and impervious hematite shell (oxidized magnetite) are developed, which may stop further oxidation of magnetite inside the core, creating a duplex structure, resulting in weakened pellets structure [25]. The dissociation temperature is decreased with impurities, such as SiO 2 , CaO, and MgO, dissociation of hematite occurs earlier [22]. While firing above 1200 • C, unreacted magnetite core and impervious hematite shell (oxidized magnetite) are developed, which may stop further oxidation of magnetite inside the core, creating a duplex structure, resulting in weakened pellets structure [25]. In the lower Blaine array (1312/1678 cm 2 /g), Iron Ore No.1 pellets were fired at 1250 • C/1300 • C, showing higher C.C.S. than the Iron Ore No.2 pellets (Blaine 1989/ 2311 cm 2 /g) due to the Ostwald ripening effect. In which finer particles, present in sufficient proportion, get consolidated faster and provide more strength to the pellets, as shown in size analysis Tables 1 and 2. Pellet M1C shows higher strength at a firing temperature of 1350 • C. For higher Blaine, the Ostwald effect does not hold satisfactory, conversely increasing fineness. Decreasing strength. Particle size analysis shows Iron Ore No.1 has 46% of 44 microns contributing to better sintering during firing. As compared to Iron Ore No.2 has a 53% of 44-micron excessive fineness makes the grains react more and, instead of transforming solid solution, liquid melt deteriorates the structure. As it can be noted from particle size analysis, more fineness in either iron ore always does not support the strength an optimal value makes the pellets strong [26,27]. The chemical composition of iron ore fines behaves differently as per the thermal treatment process of pelletization. That is the key role in forming melt phases and sintering grains. Hence, the adversity effect of constituents (SiO 2 and Al 2 O 3 ) is countable to access the economy of iron-steel production. A high composition of alumina in the ore is considered detrimental in pellet production, due to low reactivity and high viscosity of alumina. Therefore, grains are sintered without effectiveness [28]. Siliceous nature creates problems in heat interaction of particles eventually energy consumption increases for getting strength [29].
Iron Ore No.2 ore has gangue content compared to Iron ore No.1 mines as a high Al 2 O 3 /SiO 3 ratio influences the sintering of iron oxide grains, which results in the viscous melt. That enhances pore size irregularity and affects the pellet sintering [30]. Due to the low reactivity nature of alumina, high viscous melt is expected to be detrimental to the grain-matrix [28]. At high temperatures, slag phases react with alumina, forming SFCA (silico-ferrite of calcium and aluminum), which isa sintering phase with glass and poor sinter matrix strength [31]. Silica blocked the porosity and prohibited the gas flow during the hematite reduction to magnetite, affecting the formation of ý-hematite [29].  Figure 4. Besides, the porosity of the pellets, fired at 1350 • C, behave differently due to over-sintering, pore-density, or pore size irregularities. This can be seen in the grain-density analysis of SEM microstructure images in Figures 5-8. A duplex structure phenomenon and crystalline transformation generate stresses that cause micropores at a temperature above 1300 • C. The porosity of Iron Ore No.2 pellets falls on the lower side, due to the finer particle proportion of grains, contributing to the finer matrix of pore and iron oxide in the silicates melt phase [32]. The porosity of pellets is caused by various metallurgical processes. At 1250 • C, the initial oxidation and sintering of the silicate matrix, with pores and iron oxides, provide the porosity. CaO additive usage at a different temperature to form calcium ferrite and other ingredients of solid solution and space vacant behind makes pores. When CaO is exhausted, small and uniform grains are closely arranged with fine boundaries, and few porous examples have appeared [9].            The Iron Ore No.1 pellet shave good enough porosity, as compared to Iron Ore No.2 pellets. A higher melt phase influences pore formation, size irregularities, and unstable phase formation directly influence the porosity of the pellet. Porosity investigation can be done through silicate grains density, and hematite grains density is comparable between both types of pellet origin ores shown in Figure 9. Higher alumina content forms the viscous melt, which deteriorates the matrix. Further, at high-temperature, SFCA formation provides a close arrangement of grains, thereby reducing the porosity [31]. Additional silica closes the pores and reduces the porosity of the pellets, decreasing the reducibility of pellets. Silica prevents particle heat interaction and energy requirement increase. Therefore, Iron Ore No.2 has less porosity, due to high-temperature heating activating alumina as a viscous melt and filling the well-connected pores. Slag formation, due to the reaction of alumina and silica with the additive, connects pores or partially fills the pores. The Iron Ore No.1 pellet shave good enough porosity, as compared to Iron Ore No.2 pellets. A higher melt phase influences pore formation, size irregularities, and unstable phase formation directly influence the porosity of the pellet. Porosity investigation can be done through silicate grains density, and hematite grains density is comparable between both types of pellet origin ores shown in Figure 9. Higher alumina content forms the viscous melt, which deteriorates the matrix. Further, at high-temperature, SFCA formation provides a close arrangement of grains, thereby reducing the porosity [31]. Additional silica closes the pores and reduces the porosity of the pellets, decreasing the reducibility of pellets. Silica prevents particle heat interaction and energy requirement increase. Therefore, Iron Ore No.2 has less porosity, due to high-temperature heating activating alumina as a viscous melt and filling the well-connected pores. Slag formation, due to the reaction of alumina and silica with the additive, connects pores or partially fills the pores.

Microstructure Analysis
Microstructure images reveal the phase formation during thermal processing and the physico-chemical reaction. The microstructure of pellets shows, mainly, primary hematite crystal grains, which are bright with a clear triangular and rectangular shape. Crystal is compact and smooth even though no bond has been formed with grains. Secondary hematite is a bit darker and its residual surface grains have tubular massive grains. During preheating, these grains turn into reticular and vein shapes. As compared to primary grains, the angularities of the secondary hematite grains disappear or become unclear during oxidation. The transformation from massive, columnar shaped particles appeared. At the junction of secondary and primary hematite particles, microcrystalline bonding formed. Secondary hematite is more active than the primary one, mainly contributing to strength [3].
Microstructure images reveal the phase formation during thermal processing and the physico-chemical reaction. Formation of various phases of hematite appears as (grey-white), magnetite (grey-white with pinkish), pores (black shade), and silicate/slag (dark grey) in the microstructure. With its application of grain density in each phase, the size of grains and the phase's area have been analyzed. Hematite grains, under a reductive environment during heating, reduce to magnetite. This phenomenon occurs in the outer shell of pellets. Oxidation of magnetite produces secondary hematite. As Figure 8 shows, the hematite phase grain density (H.P.G.D.) is the highest at a temperature 1300 • C for the Blaine, corresponding to 200 mesh numbers for both types of ores. The high grain density of hematite depicts the high strength of pellets. Although the C.C.S. value is high for the pellet K2B, comparatively, M2B shows less H.P.G.D. due to the high Blaine 2311 cm 2 /g compared to 1678 cm 2 /g in K2B. This is so because finer particles are more active during the sintering process, and due to fineness, the distribution of grains happens more uniformly. Their distribution shows high grain density, but coarser grains with silicates support the strength. As noted, H.P.G.D. is considerably higher, in respect to Blaine fineness of the Iron Ore No.2 pellet than Iron Ore No.1 pellets, corresponding to firing temperature. The strength of pellets is the collaborative contribution of different phase proportions, with grain distribution corresponding to the firing cycle and ingredients of the pellets mixture. Here, the effect of fineness over the distribution of grains, envisaged as a finer one particle, takes part in the reaction first. Iron Ore No.1 and No.2 pellets, beyond 200 mesh H.P.G.D., decrease due to the increment of finer particle proportion. Firing at a temperature 1350 • C lowers the H.P.G.D. for both types of Iron Ore No.1 and No.2 pellets, showing that, at high temperature, high liquid melt supports faster Fe 3+ diffusion through melting, and assimilation is prevails to decrease H.P.G.D. [34].
Silicate/Slag Phase Grain Density (S.P.G.D.) The firing of flux pellets of hematite ore exhibit the following reactions. In general, heating of pellets is done at 1000 • C; here, silica and calcium start to react. Very small amounts of calcium form the dicalcium ferrite (Ca 2 Fe 2 O 5 ) phase on reaction with iron oxides. It happens only in the secondary hematite region. Calcium dissolves only 2% in magnetite concentrate. At 1100 • C, the core of pellets remain unoxidized, and silica, calcium, and iron oxides begin to react. A phase of calcium and silica-rich appears with larger silica grains. At 1150 • C, slag phases appeared more; slag phases were accommodated between the iron oxide grains. Slag phases were observed to be richer in silica than in calcium [35]. Proper grain boundaries of the silicate phase iron oxides strengthen the pellets. The S.P.G.D. decreases pore density; hence, apparent porosity (A.P.) and bulk density increase in their respective pellets, as shown in Figure 9. Finer particles in pellets have fused boundaries or assimilated phases that reduce S.P.G.D. in the microstructure [36].
Pore Phase Grains Density (P.P.G.D.) The pore phase is the second major phase, after iron oxide, and the pore phase matrix receives some reinforcement of the silicate phase. Therefore P.P.G.D. decreases as the H.P.G.D. and S.P.G.D. increase in the microstructure. Figure 10 shows that the P.P.G.D. lies on the higher side for Iron Ore No.2 pellets compared to Iron Ore No.1 pellets, due to finer particles. The CaO dissolves faster at the boundaries of smaller particles. After consumption of CaO into its ferrite form, partial or full voids are left over as pores in the matrix [37]. Since high Blaine concentrate pursues finer particles of CaO, smaller pores are formed. Thus, high pore density is achieved compared to coarse fine particles. As the Blaine increases from 1312-1678 cm 2 /g for Iron Ore No.1 pellets and 1989-2311 cm 2 /g for Iron Ore No.2 pellets, P.P.G.D. decreases. The proper sintering of oxides enhances the strength of pellets.
Further increasing Blaine increases (2425 cm 2 /g for Iron Ore No.1 pellet sand 2879 cm 2 /g for Iron Ore No.2 pellets) the P.P.G.D., due to the reactivity of finer oxide with CaO. A smaller size of partial pores appears due to the reaction, as shown in the microstructure of K3ABC and M3ABC pellets [36]. For the finest ore, the Blaine (3218 cm 2 /g for Iron Ore No.1 pellet sand 3461 cm 2 /g for Iron Ore No.2 pellets) corresponds to 400 mesh, assimilation of grains in melt occurs vigorously, phase discrimination becomes difficult even after crystallization, smaller pores become irregular, and bigger pores decrease P.P.G.D. for both Iron Ore No.1 and No.2 pellets [9].
Magnetite Phase Grain Density (M.P.G.D.) M.P.G.D. shows the rate of oxidation of reduced magnetite to secondary hematite, and the grain density of magnetite is observed significantly less as compared to other ingredients. M.P.G.D. increase as the fineness of pellets increases, due to increased resistance of oxidation from the concentric structure that pellets form. Unoxidized magnetite increases with increasing fineness; therefore, M.P.G.D. increases with fineness, which is highest for the pellets fired at 1300 • C; after that, it is highest at 1250 • C, and it is the minimum at 1350 • C for both Iron Ore No.1 and No.2 pellets. M.P.G.D. has more value in the aspect of Iron Ore No.2 due to high oxygen flow resistance. The remaining un-oxidized M.P.G.D. is high as compared to Iron Ore No.1, as shown in Figure 10. The EDS spectra is given in Table 4.

Energy Dispersive Spectroscopy (EDS) Analysis
To prove that the phases present in the pellets exhibit physical properties, characterization through microstructure and XRD analysis also chosen as supportive evidence in Figure 11. Few phases were not exhibited in the XRD analysis to support SEM images, EDS analysis provides strong evidence of their presence. As the analysis in Table 4 is shown, the iron oxide phase increases with firing temperature from 1250-1300 • C; afterward, it decreases. For these firing temperatures, ferrite phases are identified when compared to slag bonding firing at 1300 • C. While slag phases predominated when the firing took place at 1350 • C, fineness increases the bonding phase formation at all corresponding firing temperatures, as per the chemistry of the mineral present in the ore.

X-ray Diffraction Study
An XRD study has been conducted with some remarkable observations to evident the drawn conclusions from SEM analysis. In Figure 12, higher peaks of hematite, along with calcium ferrite and magnesio-ferrite, are shown. Magnetite peaks, with small heights and more in number, are observed. Quartz, along with major constituents, is shown in small quantities). K2A pellets show higher hematite and calcium ferrite peaks, supporting the microstructure images to verify the existing phases in Figure 12a. The percentage of hematite, 71.1%, and ferrite phase, 11%, were recorded. Figure 12b shows that M2A pellet structure's constituent peaks have hematite and calcium ferrite, and magnesio-ferrite forms the core matrix of pellets to provide strength. Quartz and calcium alumina ferrite, in 9%, are seen in the M2A pellet lowering strength. For the pellet K2B, XRD peaks are shown in Figure 13a. The hematite phase is a major phase (61.1%), while calcium ferrite (17%) and magnesio-ferrite (9%) are secondary phases. Few small traces of magnetite (6%) are shown to show effective oxidation. A high and broader range of peaks is strongly evident in the microstructure image analysis for the pellet's strength and porosity of pellets. Figure 13b shows the peaks of the M2B pellet's phases existing in the microstructure. The quantity of major phases reduces, while magnetite (18%) content increases concerning K2B pellets, differing in pellet strength [18].

X-ray Diffraction Study
An XRD study has been conducted with some remarkable observations to evident the drawn conclusions from SEM analysis. In Figure 12, higher peaks of hematite, along with calcium ferrite and magnesio-ferrite, are shown. Magnetite peaks, with small heights and more in number, are observed. Quartz, along with major constituents, is shown in small quantities). K2A pellets show higher hematite and calcium ferrite peaks, supporting the microstructure images to verify the existing phases in Figure 12a. The percentage of    In Figure 14, peaks of the hematite (57%), calcium ferrite (20%), and magnesio-ferrite slag phases are seen in both K2C and M2C pellets. Hematite (57%), calcium ferrite (20%), and magnesio-ferrite (15%) are observed for K2C, and hematite (67%), calcium ferrite (14.9%), and magnesio-ferrite (13.9%) are observed for M2C. Two different phases of wollastonite (5%) in K2C and wustite (4%) in M2C were observed. These phases reduce the pellet's strength and appear through prolonged magnetite reduction to wustite/wollastonite. Moreover, M2C has higher hematite due to fineness, but it shows less strength than K2C. grains, and the ferrite phase forms a matrix of hematite grains to support the stren pellets' structure and optimum porosity, as well. Although firing at 1250 °C produc lets of desirable properties, a slightly noticeable change in properties occurs due refined microstructure of clearly visible grain boundaries and well-connected phases [38]. Figure 13a,b are the peak representation of pellets K2B and M2B, respectively heights of peaks of the hematite and calcium ferrite phases are greater in number height represents the intensity of the phase available within the microstructure: he phase 61.6% of K2B; 55% of M2B and calcium ferrite phase 17% of K2B; 13% of M2B the highest strength of pellets. Only magnetite phase 9% of K2B and 14% of M2B the M2B strength, which shows that an unavoidable phenomenon occurred. Figure  and 14a,b peak availability and phase percentage are strongly evident in the micr ture phase grain density analysis to validate the physical properties (C.C.S. and A.

Fourier Transform Infrared Spectroscopy (FTIR)-Analysis
Iron Ore No.1 and No.2 pellets of the highest strength, moderate strength, hig porosity, and least strength were examined under FTIR spectroscopy in the respe chapter. Here comparative analyses concerning the abovementioned context are cussed [39] The above discussion of XRD analysis supports optimizing the firing temperature, as the firing temperature is 1350 • C, and the hematite phase % reduces, either due to the dissociation of magnetite or the reversion of hematite.
Microstructure, as appears in Figures 5d-f and 6d-f of pellets K2A, K2B, K2C, M2A, M2B, and M2C, respectively. Firing at temperature 1300 • C performs proper sintering of grains, and the ferrite phase forms a matrix of hematite grains to support the strength of pellets' structure and optimum porosity, as well. Although firing at 1250 • C produces pellets of desirable properties, a slightly noticeable change in properties occurs due to the refined microstructure of clearly visible grain boundaries and well-connected oxide phases [38]. Figure 13a,b are the peak representation of pellets K2B and M2B, respectively, as the heights of peaks of the hematite and calcium ferrite phases are greater in numbers. Peak height represents the intensity of the phase available within the microstructure: hematite phase 61.6% of K2B; 55% of M2B and calcium ferrite phase 17% of K2B; 13% of M2B shows the highest strength of pellets. Only magnetite phase 9% of K2B and 14% of M2B lower the M2B strength, which shows that an unavoidable phenomenon occurred. Figure 12a,b and Figure 14a,b peak availability and phase percentage are strongly evident in the microstructure phase grain density analysis to validate the physical properties (C.C.S. and A.P.).

Fourier Transform Infrared Spectroscopy (FTIR)-Analysis
Iron Ore No.1 and No.2 pellets of the highest strength, moderate strength, highest porosity, and least strength were examined under FTIR spectroscopy in the respective chapter. Here comparative analyses concerning the abovementioned context are discussed [39].

Highest C.C.S. Pellets
Pellets K2B and M2B have the highest C.C.S. due to significant hematite and silicate peaks with fewer peaks or ignorable peaks of hydroxyl content. Since K2B has higher C.C.S., due to the presence of the hematite compound, of 471.59 cm −1 and 550.18 cm −1 , M2B phase peaks 472.27 cm −1 and 550.44 cm −1 , with significant absorbance, as shown in Figures 15b  and 16b. Here, M2B shows a bit more absorbance due to finer grains showing abundance in the material, but K2B has a broader range. Slag/silicate phase bonds provide strength; silicate in K2B has 1016.70 cm −1 , which is broader and deeper absorbance as compared to the M2B silicate peak (1015.09 cm −1 ). The high L.O.I. hydroxyl group peak's 3438.47 cm −1 2923.2 cm −1 , weakened the structure. Pellet strength depends on the distribution of iron oxide phase grains and how they are configured in the silicate/slag phase with the pores matrix. Firing at temperature 1300 • C, physico-chemical reactions turn in the presence of coke, and various products are formed. Crystal transformation occurs swiftly, as evident in FTIR and XRD phase analysis. Iron oxide compound bonding (hematite) spectroscopy (for K2B 471.59 cm −1 and 550.18 cm −1 ; for M2B 472.27 cm −1 and 550.44 cm −1 ) was observed. Silicate/slag compound bond affiliation, denoted by the peak (for K2B 1016.70 cm −1 ; for M2B 1015.09 cm −1 ) in a broader range, shows dominance in the microstructure.   The degradation of pellets tends to generate fines under low-temperature reduction in the blast furnace. This generation of fines occurs due to various reasons, such as hematite to magnetite (hexagonal to cubic) transformation, leading to volumetric expansion. Expansion of pellet structure initiates fine crack due to stress development. For the pellets in blast furnace application, RDI in the fraction of −3.15 mm is considered, and around 20% is tolerated in blast furnace [40]. FeO percentage in the pellets influences the R.D.I., as the content is increasing with firing, as in this case for Iron Ore No.2 at 1350 • C, wustite is formed and increases the R.D.I. [41]. The formation of the melting slag phase disturbs the structure of the pellet and increases the R.D.I., as the Iron Ore No.2 pellets slag phase is higher than Iron Ore No.1 pellets, corresponding to all firing temperatures in increasing order [40,42]. Iron Ore No.2 has a higher R.D.I. compared to Iron Ore No.1, due to Al 2 O 3 content being high, as a solute in hematite responds to high R.D.I. [30]. Alumina in hematite develops a distorted weak structure at a low-temperature reduction [43,44].
The type and distribution of phases within the microstructure also reflect physicochemical properties. Microstructure analysis and XRD phase analysis validate the R.D.I. and R.I. variation in the selected pellets study. Firing at 1300 • C produces greater strength than 1250 • C but R.D.I. is increased, as per heating, due to bigger pore formation and distribution of ore, causing high R.D.I., as shown in Figure 17. Uneven, the pellet structure at high-temperature hematite ore with coke decreases the pellets' sintering; hence, R.D.I. increases. The fineness of ore and the bonds between the grains affect Porosity of pellets supports the reducibility. Carbon addition acc tions, such as hematite reduction-produced magnetite conversion which is less reducible than primary hematite because increasing lowers the reducibility. Iron Ore No.2 pellets have more fineness moval, which decreases the reducibility [21,38]. The pellets fired higher reducibility since they have a lower magnetite phase and with a higher pore phase. Pellets fired at 1350 °C have more slag pore phase, less density, and more magnetite grains, presenting shown in Figure 18 [4]. Reducibility index (R.I.) is the ease with which oxygen is removed. For good R.I., pellets should ensure enough porosity. Iron Ore No.1 pellets have coarser fines compared to Iron Ore No.2 pellets and show good apparent porosity (A.P.) and offer good R.I. As the firing temperature increases provide greater sintering and good bulk density (B.D.), it reduces the porosity; hence, R.I. decreases. Reversion of magnetite in the CaO presence produces magnetite inclusion to fulfil the intertidal between the hematite grains that are replacing oxide bonds, resulting in a weaker structure of pellets [27,45] The fineness of ore and the bonds between the grains affect the pellet's reducibility. Porosity of pellets supports the reducibility. Carbon addition accesses the various reactions, such as hematite reduction-produced magnetite conversion, to secondary hematite, which is less reducible than primary hematite because increasing the firing temperature lowers the reducibility. Iron Ore No.2 pellets have more fineness preventing oxygen removal, which decreases the reducibility [21,38]. The pellets fired at 1250 • C reflect the higher reducibility since they have a lower magnetite phase and less silicate/slag bond with a higher pore phase. Pellets fired at 1350 • C have more slag bonding with reduced pore phase, less density, and more magnetite grains, presenting the lower reducibility shown in Figure 18 [4]. The fineness of ore and the bonds between the grains affect t Porosity of pellets supports the reducibility. Carbon addition acc tions, such as hematite reduction-produced magnetite conversion, which is less reducible than primary hematite because increasing lowers the reducibility. Iron Ore No.2 pellets have more fineness moval, which decreases the reducibility [21,38]. The pellets fired higher reducibility since they have a lower magnetite phase and with a higher pore phase. Pellets fired at 1350 °C have more slag pore phase, less density, and more magnetite grains, presenting shown in Figure 18 [4]. To investigate the heating rate effect on the dissociation of the hematite oxide phase of ore. After weighing each time of the different experiments, the iron ore concentrate sample was put in an alumina pan. During heating, approximately 20 mg weight of ore was maintained, and argon gas was being blown at 200 mL/min. The reference sample of alumina powder was taken for different heating rates. In the present work, hematite ore is used and associated with dissociation at high temperatures during firing. This deteriorates the strength and reducibility of pellets. Dissociation of hematite may be, of any type, secondary or naturally present in the pellets. A researcher found hematite stability in the context of particle size and temperature. Dissociation starts at 1264 • C and ends at a temperature of 1392 • C in the air [46]. Although this is a temperature control reaction, magnetite oxidation, having an exothermic nature, makes the process complex. Thus, this is imperative to understand, comprehensively, temperature relevance with dissociation kinetics. A thermal kinetics analysis provides kinetic parameters of the reaction associated with the phenomenon. As per the availability of data and users' convenience, methods were adopted for analysis. The fitting approach model has advantages of both kinetic and mechanism process constant.
In the present study, Coats and Redfern's method is used to do a kinetic analysis of non-isothermal Thermo-Gravimetric (TGA) data [47,48]. Higher activation energy denotes strong temperature dependence of reaction. A small increment in the temperature results in faster dissociation of reaction. Three heating rates are recommended for the kinetics study to elaborate the complete course of action.
To compute the activation energy for the thermal decomposition process, leading to the formation of spinel magnetite ferrite, the TGA data has been analyzed using the Coats-Redfern method. According to the Coats-Redfern method, the mathematical relation for a first-order reaction is expressed as (1) where α is the fraction of sample decomposed at time t given by W o is the initial weight of the sample, W t represents the weight of the sample at any given temperature, and W f is sample weight after the completion of the reaction. Bis the linear heating rate, T is the absolute temperature, E a is the activation energy, A is the frequency factor, and R is the gas constant (8.314). By using Equation (1), a graph is drawn between log − log(1−α) T 2 and 1000 T . Finally, the slope of this linear graph can be written to calculate the activation energy of the reaction. For the optimality of reaction kinetics, the conversion value of 0.5 has been taken.
For the kinetics analysis of ore samples, Iron Ore No.1 and No.2 are taken off close to Blaine fineness. TGA data has been analyzed for the mass loss percentage with temperature. Figure 19 shows (i) mass percentage versus temperature graph, (ii) linear graph for Iron Ore No.1, (iii) mass percentage versus temperature graph, and (iv) linear graph for Iron Ore No.2, when heating rate 5 • C/min was considered. Similarly, Figure 19b,c show that the same mentioned parameters correspond to heating rate of 10 • C/min and 15 • C/min, respectively.  As shown in Figure 19a-c, experimental data (TGA) mass loss percentages with increasing temperatures were plotted, corresponding to heating rates 5 • C/min, 10 • C/min, 15 • C/min, respectively. Conversion (α) can be chosen concerning any temperature point on a mass percentage graph. For the sake of optimality, 0.5 conversions were chosen and correspond to this log − log(1−α) T 2 vs. 1000 T was drawn. After the linear fitting, the data slop of line is considered, as listed, in a and b in Table 5. The activation energy has been calculated as; − E a 2.303 R = slope Hematite dissociation is the undesirable reaction during induration for this nonisothermal kinetic model has taken for analysis. A small temperature change governs the hematite dissociation, along with the fineness of ore. TGA was done to get data for conducting kinetic analysis and concluded that the dissociation reaction rate is temperaturedependent: the higher the activation energy value, the higher the temperature dependence. Figure 20 shows that activation energy increases with the heating rate, influencing the hematite dissociation to become more severe with a high heating rate. As compared to Iron Ore No.2, the sample has high activation energy, corresponding to the same heating rate of Iron Ore No.1, and owing to the fineness of ore particles being high for Iron Ore No.2 compared to Iron Ore No.1.

Conclusions
The following salient points have been concluded.  Pellets roasted at 1300 °C exhibit a higher C.C.S. value than the pellets fired at other