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Effects of Fluoride and Sulphate Mineralizers on the Properties of Reconstructed Steel Slag

  • Ying Xu EMAIL logo , Shan-shan Yang , Qiao-ling Wang and Chen-guang Hu
Published/Copyright: November 14, 2019
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High Temperature Materials and Processes
From the journal High Temperature Materials and Processes Volume 38 Issue 2019

Abstract

Improving the cementitious activity and volume stability of steel slag by thermal reconstruction is an innovative method for efficient utilization of steel slag. In this study, different amounts of CaF2 and CaSO4 were added to steel slag as a mineralizer based on the determining admixtures needed for the reconstruction reaction, and the effects of CaF2 and CaSO4 on the cementitious activity and volume stability of the reconstructed steel slag were investigated. The results show that when the CaF2 content is increased to 5 wt%, the cementitious activity index of the reconstructed steel slag gradually increases to 92%, which is 12% higher than the first level technical requirement specified by the national standards, and the free CaO (f - CaO) and MgO (f-MgO) contents gradually decrease to 0.35 and 0.13 wt%, respectively. With increasing CaSO4 content, the cementitious activity index first increases and then decreases, while the contents of f -CaO and f-MgO show the opposite trend. When the CaSO4 content is 2 wt%, the activity index is 105%,which is 25%higher than the first level technical requirement specified by the national standards, and the f -CaO and f-MgO contents reach minima of 0.44 and 0.35 wt%, respectively.

Keywords: reconstructed steel slag; calcium fluoride; calcium sulphate; cementitious activity; volume stability

1 Introduction

The amount of steel slag accounts for 15%–20% of total steel production, and the annual output of steel slag in China is close to 100 million tons [1]. However, the comprehensive utilization rate of steel slag in China is only about 20% [2]. Large-scale emissions and accumulation of steel slag occupy land, pollute the environment, and cause waste of resources. By comparison, the utilization rate of steel slag in developed countries is above 95%, in which the in-plant circulation is more than 20%[3]. But steel slag from different countries is mostly used as road building materials, backfill materials, and so on, with low economic benefits. Steel slag is a potential cementitious material because it contains some minerals with cementitious activity, such as C3S, C2S, C3A, and C4AF [4]. However, there is less content of cementitious minerals in steel slag, and the mineral crystals are complete, the grains are coarse and the defects are few, which results in its low cementitious activity. Scholars have developed many kinds of steel slag activation technologies, such as mechanical activation, thermal activation, chemical activaton, and so on. But they can not fundamentally eliminate the effects of component fluctuations. Moreover, steel slag contains free CaO (f -CaO) and MgO (f-MgO), whose hydration reactions result in volume expansion of the steel slag [5]. Therefore, steel slag can not be widely used as cementing materials.

The temperature of liquid steel slag can reach 1450°C– 1650°C, and the enthalpy is up to 2000 MJ/t [6], which is a high quality waste heat resource. At present, the sensible heat recovery technology of steel slag is still in its infancy. Lots of scholars at home and abroad have studied the waste heat recovery of steel slag in vairous aspects, such as wind quenching [7], continuous casting-continuous rolling dry granulation [8], rotating-drum method, and so on. Although the researches make the waste heat of steel slag be recovered and utilized, the performance problems existing in the tailings are not solved. It is necessary to develop and popularize a technology in order to make steel slag treatment and recycling level reach the scale industrialization. In this paper, an on-line reconstruction technology of steel slag, that is, the composition and structure of

the steel slag are modified by the residual heat is proposed. That is, suitable conditioning components are added to the molten steel slag and high-temperature phase reactions between the steel slag and conditioning components occur by the waste heat of the steel slag and the composition and structure of the steel slag are regulated. This is performed to improve the cementitious activity and volume stability of steel slag.

In this process, it is important to improve the kinetic conditions of the reconstruction reaction at high temperature. Addition of a mineralizer, such as CaF2 or CaSO4, can can effectively solve this problem. Mineralizers are widely used in cement industry, and some trace elements from industrial waste can be used as mineralizers for the purpose of solid waste utilization. Scholars [9, 10, 11] found that CaF2 can decrease the temperature of phase transition and promote the formation of C3S in clinker. Kacimi, et al. [12] found that CaF2 can, in some cases, improve the hydraulic properties of Portland clinker. Horkoss et al. [13, 14] found that [SO4]2− can replace [SiO4]4− in belite, and activation of the C2S lattice can be promoted. Uda, et al. [15] suggested that SO3 can promote the absorption of f -CaO and improve the burnability of raw materials.

In summary, many experiments have proven that CaF2 and CaSO4 contribute to formation of cementitious minerals to some extent. However, there is the lack of a quantitative study of their effects on the reconstructed steel slag cementitious activity and stability, and there is no systematic study of the mechanisms of action of fluoride and sulphate mineralizers. Therefore, in this study, different amounts of CaF2 and CaSO4 were added as mineralizers to reconstructed steel slag and the effects of CaF2 and CaSO4 on the cementitious activity and volume stability of the reconstructed steel slag were investigated.

2 Experimental

2.1 Raw materials

The steel slag comes from Tangshan Iron and Steel Company, the cement is Portland cement from a cement plant in Hubei Province, the conditioning components are quicklime and slag, and the mineralizers are CaF2 and CaSO4. The chemical compositions of the raw materials are given shown in Table 1.

Table 1

Chemical compositions of the raw materials (wt%)

NameCaOSiO2Al2O3Fe2O3MgOK2ONa2OOthers
Steel slag41.4014.960.847.905.490.120.1429.15
Cement62.6021.354.673.313.080.540.214.24
Quicklime94.45——————5.55
Slag38.2028.6414.600.4210.820.440.326.56

2.2 Experimental methods

The lime saturation coefficient (KH) of the reconstructed steel slag was adjusted according to the cement clinker. The KH value of cement clinker is generally between 0.88 and 0.96. The KH value of the reconstructed steel slag was determined to be 0.9, and the specific proportions are given in Tables 2 and 3. The steel slag, quicklime, slag, and mineralizer were mixed in different proportions. The mixed raw materials were then placed in a mold for molding and forming, and the reconstructed steel slag samples were obtained. Finally, the reconstructed steel slag samples were calcined at 1400°C in a high-temperature box furnace and then cooled to about 1000°C for water quenching after holding at 1000°C for 30 min.

Table 2

Experimental proportions of the reconstructed steel slag with CaF2 samples

SampleSteel slag/wt%Quicklime/wt%Slag/wt%CaF2/wt%
K05017330
F14917331
F34916323
F54816315
Table 3

Experimental proportions of the reconstructed steel slag with CaSO4 samples

SampleSteel slag/wt%Quicklime/wt%Slag/wt%CaSO4/wt%
K05017330
L15017331
L25017322
L34916323
L44816324

The reconstructed steel slag was ground into a fine powder with a specific surface area of 400 ± 10m2/kg. The reconstituted steel slag was then mixed with cement at a mass ratio of 3:7 to prepare a steel slag–cement slurry. The compressive strength of the slurry was measured after curing in a standard maintenance room for 7 or 28 days. The cementitious activity index of the steel slag was calculated according to the relevant regulation in “Steel Slag Powder Used for Cement and Concrete” (GB/T 20491-2017) [16]:

(1)A=RtR0×100

where A is the activity index of the steel slag (%), Rt is the strength of the tested mortar at the corresponding age (MPa), and R0 is the strength of the cement mortar at the corresponding age (MPa).

The f -CaO and f-MgO contents in the reconstructed steel slag samples were measured by ethylenediaminetetraacetic acid (EDTA) chemical titration.

The stability of the reconstructed steel slag samples was tested according to the relevant regulation in the “Cement Standard Consistency, Setting Time and Stability Test Method” (GB/T 1346-2011) [17].

The microstructure, composition, and morphology of the reconstructed steel slag were analyzed by scanning electron microscopy (SEM), X-ray diffraction (XRD), and the lithofacies test.

3 Results and Discussion

3.1 Effects of fluoride and sulphate mineralizers on the cementitious activity of the reconstructed steel slag

The reconstructed steel slag samples with different CaF2 and CaSO4 contents were aged at room temperature for curing times of 7 and 28 days, respectively. The compressive strengths of the reconstructed steel slag samples aged for different times were determined and the cementitious activity index values were calculated. The results are shown in Figures 1 and 2.

Figure 1 Activity index of the reconstructed steel slag with different CaF2 contents.
Figure 1

Activity index of the reconstructed steel slag with different CaF2 contents.

Figure 2 Activity index of the reconstructed steel slag with different CaSO4 contents.
Figure 2

Activity index of the reconstructed steel slag with different CaSO4 contents.

From Figures 1 and 2, the early activity index of the reconstructed steel slag without mineralizer (K0) is 40% and the late activity index is 54%. With increasing CaF2 content, the early activity index of the reconstructed steel slag first increases and then decreases (Figure 1). When 3 wt% CaF2 is added, the early activity index reaches the highest value of 70%, which is 16% higher than that of the K0 sample and5%higher than the first level technical requirement stipulated in “Steel Slag Powder used for Cement and Concrete” (GB/T 20491-2017). When the CaF2 content exceeds 3 wt%, the early activity index gradually decreases. Because an increase in the total fluorine content in the C3S solid solution leads to a decrease in the C3S early hydration activity. The late activity index of the reconstructed steel slag gradually increases with increasing CaF2 content. When 5 wt% CaF2 is added, the late activity index reaches 92%, which is 22% higher than that of the K0 sample and 12% higher than the first level technical requirement specified in GB/T 20491-2017. However, the CaF2 content should not be too high, because when the concentration of CaF2 in the high-temperature liquid phase reaches supersaturation, it recrystallizes and increases the viscosity of the liquid phase [18]. In addition, as CaF2 volatilizes under high temperature, HF is generated by the action of high-temperature steam, which will not only pollute the environment, but also damage and corrode the refractory materials of the electric furnace used in the experiment and the containers used in in the on-line steel slag reconstruction technology [19]. Therefore, the maximum amount of CaF2 is determined to be 5 wt%. With increasing CaSO4 content, the early activity index of the reconstructed steel slag gradually increases (Figure 2). When 4 wt% CaSO4 is added, the early activity index reaches the highest value of 84%,which is 44% higher than that of the K0 sample and 19% higher than the first level technical requirement stipulated in GB/T 20491-2017. The late activity index increases and then decreases. When 2 wt% CaSO4 is added, the late activity index reaches the highest value of 105%, which is 51% higher than that of the K0 sample and 25% higher than the first level technical requirement stipulated in GB/T 20491-2017.

Mineralizers are beneficial to improve the cementitious activity of the reconstructed steel slag mainly because it promotes a decrease of viscosity. Amphoteric element Me (mainly Al3+ and Fe3+ in this system) presents different forms to maintain the acid-base equilibrium of the high temperature liquid phase. The viscosity of melt depends on [MeO4]5−⇔ [MeO6]9− equilibrium. When the complex ionic group [MeO4]5− is formed, Al3+ and Fe3+ are acidic, on the contrary, they are alkaline. [MeO4]5− is a close tetrahedral structure. The Me-O bond energy is large in [MeO4]5−, and it is not easy to break in viscous flow,which resulting in a high viscosity of the liquid phase. [MeO6]9− is a loose octahedral structure, and the viscosity of the liquid phase is smaller. F− and SO42−are both more acidic than [AlO4]5− and [FeO4]5−. Addition of F− or SO42−can promote the equilibrium to move to the right. Therefore, the viscosity of the liquid phase is reduced, and the mobility of all ions is improved [20, 21].

The cementitious activity index values of the reconstructed steel slag samples with different proportions of CaF2 and CaSO4 are higher than those of the K0 sample. The cementitious activity index of the reconstructed steel slag with CaSO4 as a mineralizer fluctuates in the range 94% to 105%. This range is higher than that of the reconstructed steel slag mixed with CaF2, which has a highest value of 92%. The results show that CaSO4 is a better mineralizer to improve the cementitious activity of steel slag than CaF2.

3.2 Effects of fluoride and sulphate mineralizers on the volume stability of the reconstructed steel slag

To test the effects of CaF2 and CaSO4 on the volume stability of the reconstructed steel slag, EDTA chemical titrations and stability tests were performed. The f -CaO and f-MgO contents are given in Tables 4 and 5, and the trends are shown in Figures 3 and 4.

Figure 3 Effect of CaF2 on the f -CaO and f-MgO contents in the reconstructed steel slag.
Figure 3

Effect of CaF2 on the f -CaO and f-MgO contents in the reconstructed steel slag.

Figure 4 Effect of CaSO4 on the f -CaO and f-MgO contents in the reconstructed steel slag.
Figure 4

Effect of CaSO4 on the f -CaO and f-MgO contents in the reconstructed steel slag.

Table 4

Effect of CaF2 on the f -CaO and f-MgO contents in the reconstructed steel slag

SampleCaF2 content/wt%f -CaO/wt%f -MgO/wt%
K000.510.36
F110.480.30
F330.440.22
F550.350.13
Table 5

Effect of CaSO4 on the f -CaO and f-MgO contents in the reconstructed steel slag

SampleCaSO4 content/wt%f -CaO/wt%f -MgO/wt%
K000.510.36
L110.470.34
L220.360.30
L330.430.33
L440.440.35

From Tables 4 and 5, the f -CaO and f-MgO contents are all less than 2 wt%, which is within the standard range of good stability.

With increasing CaF2 content, the f -CaO and f-MgO contents in the reconstructed steel slag linearly decrease (Figure 3). The f -CaO content decreases from 0.51 to 0.35 wt% and the f-MgO content decreases from 0.36 to 0.13 wt%. The f -CaO and f-MgO contents first decrease and then increase with increasing CaSO4 content (Figure 4). When the content of CaSO4 is 2 wt%, the f -CaO content decreases from 0.51 (without CaSO4) to 0.36 wt% and the f - MgO content decreases from 0.36 (without CaSO4) to 0.30 wt%. The f -CaO and f-MgO contents in the reconstructed slag samples with mineralizer are all lower than those of the K0 sample.

Addition of CaF2 and CaSO4 reduces the viscosity of the steel slag, which results in more f -CaO participating in the reactions to form C2S and C3S. In addition, CaF2 and CaSO4 promote the dissolution of f-MgO in gelling minerals, and the reasons are as follows. When S and F are dissolved into C3S crystal respectively, S6+ displaces Si4+ and F− displaces O2−. In order to balance the electricity price, the vacancy reaction in C3S is likely to occur in the form of co-substitution of different price ions [22].

SO3+Al2O3→C3SSSi⋅⋅+2AlSi,+6O0
CaF2+Al2O3→C3S2AlSi,+2F0⋅+CaCa+3O0

As shown above, Al3+ participates in the substitution reaction together with S6+ or F−. Thus, the Al3+ content in the C3S solid solution increases, which leads to the change of crystal structure of C3S. The ionic radius of Si4+ is 0.26 nm and that of Al3+ is 0.39 nm. When Al3+ replaces Si4+ and enters Si-O tetrahedron, the space of Si-O tetrahedron will be enlarged, which may indirectly cause the deformation of adjacent Ca-O octahedron. MgO and CaO have the same configuration, and the ionic radius of Mg2+ is 0.72 nm and that of Ca2+ is 1.0 nm. Therefore, Mg2+ with a smaller ion radius is more likely to replace the Ca2+ ions in C3S lattice to form solid solution in order to keep the banlance of the structure [23].

CaF2 and CaSO4 have similar effects on the f -CaO content in the reconstructed steel slag, but the f-MgO content in the reconstructed steel slag with CaF2 is lower than that with CaSO4. The f -CaO and f-MgO contents in the reconstructed slag with CaF2 are lower than those with CaSO4 at the optimal amount of mineralizer,which indicates that addition of CaF2 as a mineralizer to improve the stability of steel slag is better than addition of CaSO4.

Considering the effects of CaF2 and CaSO4 on the cementitious activity and volume stability of the reconstructed steel slag, the optimum contents of CaF2 and CaSO4 in the reconstructed steel slag are 5 and 2 wt%, respectively.

The stability of the reconstructed steel slag with CaF2 and CaSO4 was tested by boiling experiments, and the results are shown in Figure 5. The reconstructed steel slag test cake surfaces are smooth with no cracks, and the test cakes can be completely removed from the glass sheets. This shows that the volume stability of the reconstructed steel slag is up to standard.

Figure 5 Soundness test cakes of the reconstructed steel slag.
Figure 5

Soundness test cakes of the reconstructed steel slag.

3.3 Effects of fluoride and sulphate mineralizers on the composition and morphology of the reconstructed steel slag

The XRD patterns of the reconstructed steel slag with different CaF2 and CaSO4 contents are shown in Figures 6 and 7, respectively. The diffraction peaks of the three cementing minerals C2S, C3S, and C3A are present for the reconstructed steel slag samples (Figure 6).However, the diffraction peaks of these three minerals are weaker for the reconstructed steel slag without CaF2 than for the other steel slag samples, and the peaks of the RO phase are present. For the reconstructed steel slag with CaF2, the diffraction peaks of the RO phase are absent but the diffraction peaks of C4AF and C2F are present, which indicates that CaF2 is helpful to decompose the RO phase. FeOx from decomposition of the RO phase reacts with calcium and aluminum oxide to form C4AF and C2F. The diffraction peaks of C2S gradually decreases and the diffraction peaks of C3S and C3A gradually increases when the CaF2 content exceeds 1 wt%, indicating that CaF2 promotes the reactions of C2S and Al2O3 with CaO to form C3S and C3A, respectively. As shown in Figure 7, the main cementitious minerals of the reconstructed steel slag with CaSO4 are C3S, C2S, C3A, and C2F. The diffraction peaks of the RO phase are absent. FeOx from decomposition the RO phase mainly reacts with CaO to produce C2F. As the amount of CaSO4 increases, the C3A content gradually increases, and the C3S and C2S contents first increase and then decrease. When 2 wt% CaSO4 is added, the diffraction peaks of the main cementitious minerals, such as C3S and C2S, are the most acute. This is because of the excessive amount of SO3 generated from CaSO4 under high temperature stabilizes C2S and prevents absorption of f -CaO by C2S,which are not conducive to formation of C3S [24].

Figure 6 XRD patterns of reconstructed steel slag with different CaF2 contents.
Figure 6

XRD patterns of reconstructed steel slag with different CaF2 contents.

Figure 7 XRD patterns of reconstructed steel slag with different CaSO4 contents.
Figure 7

XRD patterns of reconstructed steel slag with different CaSO4 contents.

SEM images of the reconstructed steel slag with different CaF2 and CaSO4 contents are shown in Figures 8 and 9, respectively. The minerals in the reconstructed steel slag without CaF2 are in the form of loose short rods. With increasing CaF2 content, the minerals are gradually refined, and some minerals begin to exist in a melting state. When the CaF2 content is 5 wt%, the minerals are in the melting state. Some of them have fish scale or droplet shapes, which are determined to be mainly C3S, C3A and C2F according to energy spectrum analysis. The mineral structure is dense and uniform, and there are fewer pores and more liquid phase in the steel slag sample. When the CaSO4 content is 2 wt%, the reconstructed steel slag has a better melting state and more liquid phase (Figure 9).Moreover, there is more C2S and C3S, whose grain shapes tend to be complete and the grain boundaries are clear. The reason why CaF2 or CaSO4 increases the amount of liquid phase is that the addition of them increases the composition of the system, and greatly reduces the minimum eutectic temperature and the liquid phase appearance temperature.

Figure 8 SEM images of reconstructed steel slag with different CaF2 contents. (a) 0, (b) 1, (c) 3, and (d) 5 wt% CaF2.
Figure 8

SEM images of reconstructed steel slag with different CaF2 contents. (a) 0, (b) 1, (c) 3, and (d) 5 wt% CaF2.

Figure 9 SEM images of reconstructed steel slag with different CaSO4 contents. (a) 1, (b) 2, (c) 3, and (d) 4 wt% CaSO4.
Figure 9

SEM images of reconstructed steel slag with different CaSO4 contents. (a) 1, (b) 2, (c) 3, and (d) 4 wt% CaSO4.

The lithofacies test images of the reconstructed steel slag with different CaF2 and CaSO4 contents are shown in Figures 10 and 11, respectively. The minerals in the steel slag without CaF2 are coarse, varied in shape, and loose in arrangement (Figure 10). After addition of CaF2, the main minerals in the reconstructed steel slag include cross bicrystalline, round-grained, or elliptical β-C2S, hexagonal or long-flake C3S, and gray acicular or dendritic C2F and C4AF. With increasing CaF2 content, the particles of C3S and C2S increase and are significantly refined. When the CaF2 content is 5 wt%, club-shaped C3S and round-grained C2S show a uniform agglomeration distribution. When the content of CaSO4 is 2 wt%, a large number of round or elliptical C2S and hexagonal C3S particles appear with a uniform distribution and high degree of crystallization (Figure 11b). In addition, scattered white sheet minerals are observed in the reconstructed steel slag doped with CaF2 and CaSO4. An energy dispersive spectroscopy (EDS) test of this substance was performed (Figure 12). From EDS and XRD analysis, it is concluded that the white sheet mineral is MgFe2O4 formed by the reaction of FeOx and MgO from decomposition of the RO phase solid solution. This is also a reason for reduction of f-MgO.

Figure 10 Lithofacies test images of reconstructed steel slag with different of CaF2 contents. (a) 0, (b) 1, (c) 3, and (d) 5 wt% CaF2.
Figure 10

Lithofacies test images of reconstructed steel slag with different of CaF2 contents. (a) 0, (b) 1, (c) 3, and (d) 5 wt% CaF2.

Figure 11 Lithofacies test images of reconstructed steel slag with different CaSO4 contents. (a) 0, (b) 2, (c) 3, and (d) 4 wt% CaSO4.
Figure 11

Lithofacies test images of reconstructed steel slag with different CaSO4 contents. (a) 0, (b) 2, (c) 3, and (d) 4 wt% CaSO4.

Figure 12 EDS energy spectrum of the reconstructed steel slag.
Figure 12

EDS energy spectrum of the reconstructed steel slag.

3.4 Mechanisms of the effects of fluoride and sulphate mineralizers on the hydration activity of the reconstructed steel slag

Strength development and the volume stability of steel slag are strongly affected by the hydration mechanisms of the cementitious minerals and the microstructures of the hydration products. The hydration reactions of the cementitious minerals at room temperature are

C3S:

C3S + nH→ C–S–H + (3-x)CH

C2S:

C2S + mH→ C–S–H + (2-x)CH

C3A:

C3A + CH + 12H→ C4AH13

When CaSO4 exists:

C4AH13 + 3CSH2 + 14H→ C3A·3CS·H32

C4AF:

C4AF + 4CH + 22H→ 2C4(A,F)H13

When CaSO4 exists:

C4AF + 2CH + 6CSH2 + 50H→ 2C3(A,F)·3CS·H32

When steel slag–cement is mixed with water, C3A is hydrated first and the hydration reaction is severe. Hydration of C4AF and C3S then occurs, and hydration of C2S finally occurs because it has the slowest hydration rate.Hydrated calcium silicate (C–S–H), the hydration product of C2S and C3S, is the most abundant mineral in hardened steel slag–cement slurry and it plays a major role in its strength. Ca(OH)2, another hydration product of C2S and C3S, affects the strength by closely intertwining with C– S–H gel. The high hydration rate and high early strength of C3S make it the main material that determines the early strength of steel slag. In the presence of CaSO4, hydrated calcium sulphoaluminate (also known as AFt), the hydration product of C3A, also plays a role in the early strength. C3S not only has high early strength, but it also has good late strength development. The effect of C2S on the strength is not great until the late stage. Thus, the late strength is mainly affected by C2S and C3S. C4AF has a favorable effect on the sulfate resistance properties, but it has little effect on the strength.

The hydration process is the comprehensive action of mineral hydration, which is different from the general chemical reaction in solution or liquid. In particular, migration of ions is difficult and they cannot completely participate in the reaction in a short time. Instead, ions start from the surface and slowly migrate into the center by diffusion under the condition of constantly changing concentration. In this process, the change in the mineral composition of the reconstructed steel slag caused by participation of the mineralizer has a different effect on the hydration process and strength of the steel slag in different periods.

Mineralizer improves the early strength of the C2S slurry. This is because the C–S–H gel produced by early C2S hydration has a large specific surface area, which make F− or SO42−adsorb on the gel surface and precipitation of the gel on unhydrated particles surface is reduced, and C–S–H is immediately isolated once formed. The hydration reaction of C2S is then accelerated and the amount of C–S–H gel increases. The mineralizer can also decrease the distortion degree of the C3S crystal, and the symmetry of the C3S crystal structure increases. Moreover, with increasing F− or SO3 content in C3S solution, Ca(OH)2 supersaturation becomes slow, and crystallization and nucleation growth of Ca(OH)2 is delayed. Therefore, mineralizer can reduce the early hydration rate of C3S. In the latter stages of hydration, the mineralizer also enables C– S–H to grow to elongated fibers, which cross and overlap, resulting in a denser and harder hydration product structure. The strength of C3A especially increases when CaSO4 is added. This is because AFt can form a diffusion barrier on the surface of C3A particles to slow down the hydration reaction, smooth heat release, and greatly reduce the probability of crack generation.

3.5 3.5 Potential applications and prospects

It is found that the interior of the slag block is still red-hot when turning over slag and cracking the large slag block. It can be seen that the steel slag has a large thermal capacity, and the steel slag in the middle can maintain a high temperature state for a long time. However, the aim of steel-making is to control the quality of steel, thus, the composition, the viscosity and the temperature range of liquid phase of steel slag in each furnace sometimes vary [25]. If the viscosity is large and the temperature range of the liquid phase is narrow, it is not conducive to the reconstruction reaction of steel slag. Addition of mineralizers based on the determining admixtures needed for the reconstruction reaction can reduce viscosity and increase the temperature range of liquid phase and make the reconstitution reaction more thorough.

The on-line reconstruction of steel slag makes use of residual heat of steel slag and improves its cementitious and stable properties at the same time. This study provides a theoretical basis for the high efficiency application of low activity metallurgical slag in building materials industry. It is beneficial to promote energy saving and emission reduction, and to reduce environmental pollution.

4 Conclusion

With increasing CaF2 content, the early activity index of the reconstructed steel slag first increases and then decreases. When 3 wt% CaF2 is added, the early activity index reaches the highest value of 70%, which is 5% higher than the first level technical requirement stipulated by the national standards. The late activity index gradually increases with increasing CaF2 content, and it reaches the highest value of 92% with addition of 5 wt% CaF2. This value is 12% higher than the first level technical requirement. The f -CaO and f-MgO contents gradually decrease with addition of CaF2. When the CaF2 content is 5 wt%, the f -CaO and f-MgO contents reach the lowest values of 0.35 and 0.13 wt%, respectively. After adding CaF2 to the reconstructed steel slag, the RO phase decomposes and C2F and C4AF are generated. The C3S and C3A contents in the reconstructed steel slag gradually increase and the particles of the cementitious minerals are finer and more evenly distributed. The optimum dosage of CaF2 is 5 wt%.

With increasing CaSO4 content, the early activity index of the reconstructed steel slag gradually increases. When 4 wt% CaSO4 is added, the early activity index reaches the highest value of 84%, which is 19% higher than the first level technical requirement. The late activity index of the reconstructed steel slag first increases and then decrease. When 2 wt% CaSO4 is added, the late activity index reaches the highest value of 105%, which is 25% higher than the first level technical requirement. The f -CaO and f-MgO contents first increase and then decrease with increasing addition of CaSO4. When the CaSO4 content is 2 wt%, the f -CaO and f-MgO contents reach the lowest values of 0.44 and 0.35 wt%, respectively. After adding CaSO4 to the reconstructed steel slag, the RO phase decomposes and C2F is generated. The optimum dosage of CaSO4 is 2 wt%.

The effect of CaSO4 as a mineralizer to improve the cementitious activity of steel slag is better than that of CaF2. In contrast, the effect of CaF2 as a mineralizer to improve the stability of steel slag is better than that of CaSO4.

The on-line reconstruction of steel slag is an efficient way to utilize steel slag by making full use of the residual heat of molten steel slag and modifying the steel slag. And the gelling activity and voluem stability of steel slag is improved. This paper provides a theoretical basis for the high efficiency application of steel slag. It is beneficial to reduce environmental pollution and waste of resources.

Acknowledgement

This research was supported by the financial support ofNationalNatural Science Foundation of China (51574109), and Hebei provincial Key Laboratory of Inorganic Nonmetallic Materials, College of Materials Science and Engineering, North China University of Science and Technology.

We thank Liwen Bianji, Edanz Group China (www.liwenbianji.cn/ac) for editing the English text of a draft of this manuscript.

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Received: 2019-03-09
Accepted: 2019-06-10
Published Online: 2019-11-14
Published in Print: 2019-02-25

© 2019 Y. Xu et al., published by De Gruyter

This work is licensed under the Creative Commons Attribution 4.0 Public License.

Articles in the same Issue

  1. Frontmatter
  2. Review Article
  3. Research on the Influence of Furnace Structure on Copper Cooling Stave Life
  4. Influence of High Temperature Oxidation on Hydrogen Absorption and Degradation of Zircaloy-2 and Zr 700 Alloys
  5. Correlation between Travel Speed, Microstructure, Mechanical Properties and Wear Characteristics of Ni-Based Hardfaced Deposits over 316LN Austenitic Stainless Steel
  6. Factors Influencing Gas Generation Behaviours of Lump Coal Used in COREX Gasifier
  7. Experiment Research on Pulverized Coal Combustion in the Tuyere of Oxygen Blast Furnace
  8. Phosphate Capacities of CaO–FeO–SiO2–Al2O3/Na2O/TiO2 Slags
  9. Microstructure and Interface Bonding Strength of WC-10Ni/NiCrBSi Composite Coating by Vacuum Brazing
  10. Refill Friction Stir Spot Welding of Dissimilar 6061/7075 Aluminum Alloy
  11. Solvothermal Synthesis and Magnetic Properties of Monodisperse Ni0.5Zn0.5Fe2O4 Hollow Nanospheres
  12. On the Capability of Logarithmic-Power Model for Prediction of Hot Deformation Behavior of Alloy 800H at High Strain Rates
  13. 3D Heat Conductivity Model of Mold Based on Node Temperature Inheritance
  14. 3D Microstructure and Micromechanical Properties of Minerals in Vanadium-Titanium Sinter
  15. Effect of Martensite Structure and Carbide Precipitates on Mechanical Properties of Cr-Mo Alloy Steel with Different Cooling Rate
  16. The Interaction between Erosion Particle and Gas Stream in High Temperature Gas Burner Rig for Thermal Barrier Coatings
  17. Permittivity Study of a CuCl Residue at 13–450 °C and Elucidation of the Microwave Intensification Mechanism for Its Dechlorination
  18. Study on Carbothermal Reduction of Titania in Molten Iron
  19. The Sequence of the Phase Growth during Diffusion in Ti-Based Systems
  20. Growth Kinetics of CoB–Co2B Layers Using the Powder-Pack Boriding Process Assisted by a Direct Current Field
  21. High-Temperature Flow Behaviour and Constitutive Equations for a TC17 Titanium Alloy
  22. Research on Three-Roll Screw Rolling Process for Ti6Al4V Titanium Alloy Bar
  23. Continuous Cooling Transformation of Undeformed and Deformed High Strength Crack-Arrest Steel Plates for Large Container Ships
  24. Formation Mechanism and Influence Factors of the Sticker between Solidified Shell and Mold in Continuous Casting of Steel
  25. Casting Defects in Transition Layer of Cu/Al Composite Castings Prepared Using Pouring Aluminum Method and Their Formation Mechanism
  26. Effect of Current on Segregation and Inclusions Characteristics of Dual Alloy Ingot Processed by Electroslag Remelting
  27. Investigation of Growth Kinetics of Fe2B Layers on AISI 1518 Steel by the Integral Method
  28. Microstructural Evolution and Phase Transformation on the X-Y Surface of Inconel 718 Ni-Based Alloys Fabricated by Selective Laser Melting under Different Heat Treatment
  29. Characterization of Mn-Doped Co3O4 Thin Films Prepared by Sol Gel-Based Dip-Coating Process
  30. Deposition Characteristics of Multitrack Overlayby Plasma Transferred Arc Welding on SS316Lwith Co-Cr Based Alloy – Influence ofProcess Parameters
  31. Elastic Moduli and Elastic Constants of Alloy AuCuSi With FCC Structure Under Pressure
  32. Effect of Cl on Softening and Melting Behaviors of BF Burden
  33. Effect of MgO Injection on Smelting in a Blast Furnace
  34. Structural Characteristics and Hydration Kinetics of Oxidized Steel Slag in a CaO-FeO-SiO2-MgO System
  35. Optimization of Microwave-Assisted Oxidation Roasting of Oxide–Sulphide Zinc Ore with Addition of Manganese Dioxide Using Response Surface Methodology
  36. Hydraulic Study of Bubble Migration in Liquid Titanium Alloy Melt during Vertical Centrifugal Casting Process
  37. Investigation on Double Wire Metal Inert Gas Welding of A7N01-T4 Aluminum Alloy in High-Speed Welding
  38. Oxidation Behaviour of Welded ASTM-SA210 GrA1 Boiler Tube Steels under Cyclic Conditions at 900°C in Air
  39. Study on the Evolution of Damage Degradation at Different Temperatures and Strain Rates for Ti-6Al-4V Alloy
  40. Pack-Boriding of Pure Iron with Powder Mixtures Containing ZrB2
  41. Evolution of Interfacial Features of MnO-SiO2 Type Inclusions/Steel Matrix during Isothermal Heating at Low Temperatures
  42. Effect of MgO/Al2O3 Ratio on Viscosity of Blast Furnace Primary Slag
  43. The Microstructure and Property of the Heat Affected zone in C-Mn Steel Treated by Rare Earth
  44. Microwave-Assisted Molten-Salt Facile Synthesis of Chromium Carbide (Cr3C2) Coatings on the Diamond Particles
  45. Effects of B on the Hot Ductility of Fe-36Ni Invar Alloy
  46. Impurity Distribution after Solidification of Hypereutectic Al-Si Melts and Eutectic Al-Si Melt
  47. Induced Electro-Deposition of High Melting-Point Phases on MgO–C Refractory in CaO–Al2O3–SiO2 – (MgO) Slag at 1773 K
  48. Microstructure and Mechanical Properties of 14Cr-ODS Steels with Zr Addition
  49. A Review of Boron-Rich Silicon Borides Basedon Thermodynamic Stability and Transport Properties of High-Temperature Thermoelectric Materials
  50. Siliceous Manganese Ore from Eastern India:A Potential Resource for Ferrosilicon-Manganese Production
  51. A Strain-Compensated Constitutive Model for Describing the Hot Compressive Deformation Behaviors of an Aged Inconel 718 Superalloy
  52. Surface Alloys of 0.45 C Carbon Steel Produced by High Current Pulsed Electron Beam
  53. Deformation Behavior and Processing Map during Isothermal Hot Compression of 49MnVS3 Non-Quenched and Tempered Steel
  54. A Constitutive Equation for Predicting Elevated Temperature Flow Behavior of BFe10-1-2 Cupronickel Alloy through Double Multiple Nonlinear Regression
  55. Oxidation Behavior of Ferritic Steel T22 Exposed to Supercritical Water
  56. A Multi Scale Strategy for Simulation of Microstructural Evolutions in Friction Stir Welding of Duplex Titanium Alloy
  57. Partition Behavior of Alloying Elements in Nickel-Based Alloys and Their Activity Interaction Parameters and Infinite Dilution Activity Coefficients
  58. Influence of Heating on Tensile Physical-Mechanical Properties of Granite
  59. Comparison of Al-Zn-Mg Alloy P-MIG Welded Joints Filled with Different Wires
  60. Microstructure and Mechanical Properties of Thick Plate Friction Stir Welds for 6082-T6 Aluminum Alloy
  61. Research Article
  62. Kinetics of oxide scale growth on a (Ti, Mo)5Si3 based oxidation resistant Mo-Ti-Si alloy at 900-1300∘C
  63. Calorimetric study on Bi-Cu-Sn alloys
  64. Mineralogical Phase of Slag and Its Effect on Dephosphorization during Converter Steelmaking Using Slag-Remaining Technology
  65. Controllability of joint integrity and mechanical properties of friction stir welded 6061-T6 aluminum and AZ31B magnesium alloys based on stationary shoulder
  66. Cellular Automaton Modeling of Phase Transformation of U-Nb Alloys during Solidification and Consequent Cooling Process
  67. The effect of MgTiO3Adding on Inclusion Characteristics
  68. Cutting performance of a functionally graded cemented carbide tool prepared by microwave heating and nitriding sintering
  69. Creep behaviour and life assessment of a cast nickel – base superalloy MAR – M247
  70. Failure mechanism and acoustic emission signal characteristics of coatings under the condition of impact indentation
  71. Reducing Surface Cracks and Improving Cleanliness of H-Beam Blanks in Continuous Casting — Improving continuous casting of H-beam blanks
  72. Rhodium influence on the microstructure and oxidation behaviour of aluminide coatings deposited on pure nickel and nickel based superalloy
  73. The effect of Nb content on precipitates, microstructure and texture of grain oriented silicon steel
  74. Effect of Arc Power on the Wear and High-temperature Oxidation Resistances of Plasma-Sprayed Fe-based Amorphous Coatings
  75. Short Communication
  76. Novel Combined Feeding Approach to Produce Quality Al6061 Composites for Heat Sinks
  77. Research Article
  78. Micromorphology change and microstructure of Cu-P based amorphous filler during heating process
  79. Controlling residual stress and distortion of friction stir welding joint by external stationary shoulder
  80. Research on the ingot shrinkage in the electroslag remelting withdrawal process for 9Cr3Mo roller
  81. Production of Mo2NiB2 Based Hard Alloys by Self-Propagating High-Temperature Synthesis
  82. The Morphology Analysis of Plasma-Sprayed Cast Iron Splats at Different Substrate Temperatures via Fractal Dimension and Circularity Methods
  83. A Comparative Study on Johnson–Cook, Modified Johnson–Cook, Modified Zerilli–Armstrong and Arrhenius-Type Constitutive Models to Predict Hot Deformation Behavior of TA2
  84. Dynamic absorption efficiency of paracetamol powder in microwave drying
  85. Preparation and Properties of Blast Furnace Slag Glass Ceramics Containing Cr2O3
  86. Influence of unburned pulverized coal on gasification reaction of coke in blast furnace
  87. Effect of PWHT Conditions on Toughness and Creep Rupture Strength in Modified 9Cr-1Mo Steel Welds
  88. Role of B2O3 on structure and shear-thinning property in CaO–SiO2–Na2O-based mold fluxes
  89. Effect of Acid Slag Treatment on the Inclusions in GCr15 Bearing Steel
  90. Recovery of Iron and Zinc from Blast Furnace Dust Using Iron-Bath Reduction
  91. Phase Analysis and Microstructural Investigations of Ce2Zr2O7 for High-Temperature Coatings on Ni-Base Superalloy Substrates
  92. Combustion Characteristics and Kinetics Study of Pulverized Coal and Semi-Coke
  93. Mechanical and Electrochemical Characterization of Supersolidus Sintered Austenitic Stainless Steel (316 L)
  94. Synthesis and characterization of Cu doped chromium oxide (Cr2O3) thin films
  95. Ladle Nozzle Clogging during casting of Silicon-Steel
  96. Thermodynamics and Industrial Trial on Increasing the Carbon Content at the BOF Endpoint to Produce Ultra-Low Carbon IF Steel by BOF-RH-CSP Process
  97. Research Article
  98. Effect of Boundary Conditions on Residual Stresses and Distortion in 316 Stainless Steel Butt Welded Plate
  99. Numerical Analysis on Effect of Additional Gas Injection on Characteristics around Raceway in Melter Gasifier
  100. Variation on thermal damage rate of granite specimen with thermal cycle treatment
  101. Effects of Fluoride and Sulphate Mineralizers on the Properties of Reconstructed Steel Slag
  102. Effect of Basicity on Precipitation of Spinel Crystals in a CaO-SiO2-MgO-Cr2O3-FeO System
  103. Review Article
  104. Exploitation of Mold Flux for the Ti-bearing Welding Wire Steel ER80-G
  105. Research Article
  106. Furnace heat prediction and control model and its application to large blast furnace
  107. Effects of Different Solid Solution Temperatures on Microstructure and Mechanical Properties of the AA7075 Alloy After T6 Heat Treatment
  108. Study of the Viscosity of a La2O3-SiO2-FeO Slag System
  109. Tensile Deformation and Work Hardening Behaviour of AISI 431 Martensitic Stainless Steel at Elevated Temperatures
  110. The Effectiveness of Reinforcement and Processing on Mechanical Properties, Wear Behavior and Damping Response of Aluminum Matrix Composites
https://doi.org/10.1515/htmp-2019-0036
Keywords for this article
reconstructed steel slag; calcium fluoride; calcium sulphate; cementitious activity; volume stability
Creative Commons
BY 4.0

Articles in the same Issue

  1. Frontmatter
  2. Review Article
  3. Research on the Influence of Furnace Structure on Copper Cooling Stave Life
  4. Influence of High Temperature Oxidation on Hydrogen Absorption and Degradation of Zircaloy-2 and Zr 700 Alloys
  5. Correlation between Travel Speed, Microstructure, Mechanical Properties and Wear Characteristics of Ni-Based Hardfaced Deposits over 316LN Austenitic Stainless Steel
  6. Factors Influencing Gas Generation Behaviours of Lump Coal Used in COREX Gasifier
  7. Experiment Research on Pulverized Coal Combustion in the Tuyere of Oxygen Blast Furnace
  8. Phosphate Capacities of CaO–FeO–SiO2–Al2O3/Na2O/TiO2 Slags
  9. Microstructure and Interface Bonding Strength of WC-10Ni/NiCrBSi Composite Coating by Vacuum Brazing
  10. Refill Friction Stir Spot Welding of Dissimilar 6061/7075 Aluminum Alloy
  11. Solvothermal Synthesis and Magnetic Properties of Monodisperse Ni0.5Zn0.5Fe2O4 Hollow Nanospheres
  12. On the Capability of Logarithmic-Power Model for Prediction of Hot Deformation Behavior of Alloy 800H at High Strain Rates
  13. 3D Heat Conductivity Model of Mold Based on Node Temperature Inheritance
  14. 3D Microstructure and Micromechanical Properties of Minerals in Vanadium-Titanium Sinter
  15. Effect of Martensite Structure and Carbide Precipitates on Mechanical Properties of Cr-Mo Alloy Steel with Different Cooling Rate
  16. The Interaction between Erosion Particle and Gas Stream in High Temperature Gas Burner Rig for Thermal Barrier Coatings
  17. Permittivity Study of a CuCl Residue at 13–450 °C and Elucidation of the Microwave Intensification Mechanism for Its Dechlorination
  18. Study on Carbothermal Reduction of Titania in Molten Iron
  19. The Sequence of the Phase Growth during Diffusion in Ti-Based Systems
  20. Growth Kinetics of CoB–Co2B Layers Using the Powder-Pack Boriding Process Assisted by a Direct Current Field
  21. High-Temperature Flow Behaviour and Constitutive Equations for a TC17 Titanium Alloy
  22. Research on Three-Roll Screw Rolling Process for Ti6Al4V Titanium Alloy Bar
  23. Continuous Cooling Transformation of Undeformed and Deformed High Strength Crack-Arrest Steel Plates for Large Container Ships
  24. Formation Mechanism and Influence Factors of the Sticker between Solidified Shell and Mold in Continuous Casting of Steel
  25. Casting Defects in Transition Layer of Cu/Al Composite Castings Prepared Using Pouring Aluminum Method and Their Formation Mechanism
  26. Effect of Current on Segregation and Inclusions Characteristics of Dual Alloy Ingot Processed by Electroslag Remelting
  27. Investigation of Growth Kinetics of Fe2B Layers on AISI 1518 Steel by the Integral Method
  28. Microstructural Evolution and Phase Transformation on the X-Y Surface of Inconel 718 Ni-Based Alloys Fabricated by Selective Laser Melting under Different Heat Treatment
  29. Characterization of Mn-Doped Co3O4 Thin Films Prepared by Sol Gel-Based Dip-Coating Process
  30. Deposition Characteristics of Multitrack Overlayby Plasma Transferred Arc Welding on SS316Lwith Co-Cr Based Alloy – Influence ofProcess Parameters
  31. Elastic Moduli and Elastic Constants of Alloy AuCuSi With FCC Structure Under Pressure
  32. Effect of Cl on Softening and Melting Behaviors of BF Burden
  33. Effect of MgO Injection on Smelting in a Blast Furnace
  34. Structural Characteristics and Hydration Kinetics of Oxidized Steel Slag in a CaO-FeO-SiO2-MgO System
  35. Optimization of Microwave-Assisted Oxidation Roasting of Oxide–Sulphide Zinc Ore with Addition of Manganese Dioxide Using Response Surface Methodology
  36. Hydraulic Study of Bubble Migration in Liquid Titanium Alloy Melt during Vertical Centrifugal Casting Process
  37. Investigation on Double Wire Metal Inert Gas Welding of A7N01-T4 Aluminum Alloy in High-Speed Welding
  38. Oxidation Behaviour of Welded ASTM-SA210 GrA1 Boiler Tube Steels under Cyclic Conditions at 900°C in Air
  39. Study on the Evolution of Damage Degradation at Different Temperatures and Strain Rates for Ti-6Al-4V Alloy
  40. Pack-Boriding of Pure Iron with Powder Mixtures Containing ZrB2
  41. Evolution of Interfacial Features of MnO-SiO2 Type Inclusions/Steel Matrix during Isothermal Heating at Low Temperatures
  42. Effect of MgO/Al2O3 Ratio on Viscosity of Blast Furnace Primary Slag
  43. The Microstructure and Property of the Heat Affected zone in C-Mn Steel Treated by Rare Earth
  44. Microwave-Assisted Molten-Salt Facile Synthesis of Chromium Carbide (Cr3C2) Coatings on the Diamond Particles
  45. Effects of B on the Hot Ductility of Fe-36Ni Invar Alloy
  46. Impurity Distribution after Solidification of Hypereutectic Al-Si Melts and Eutectic Al-Si Melt
  47. Induced Electro-Deposition of High Melting-Point Phases on MgO–C Refractory in CaO–Al2O3–SiO2 – (MgO) Slag at 1773 K
  48. Microstructure and Mechanical Properties of 14Cr-ODS Steels with Zr Addition
  49. A Review of Boron-Rich Silicon Borides Basedon Thermodynamic Stability and Transport Properties of High-Temperature Thermoelectric Materials
  50. Siliceous Manganese Ore from Eastern India:A Potential Resource for Ferrosilicon-Manganese Production
  51. A Strain-Compensated Constitutive Model for Describing the Hot Compressive Deformation Behaviors of an Aged Inconel 718 Superalloy
  52. Surface Alloys of 0.45 C Carbon Steel Produced by High Current Pulsed Electron Beam
  53. Deformation Behavior and Processing Map during Isothermal Hot Compression of 49MnVS3 Non-Quenched and Tempered Steel
  54. A Constitutive Equation for Predicting Elevated Temperature Flow Behavior of BFe10-1-2 Cupronickel Alloy through Double Multiple Nonlinear Regression
  55. Oxidation Behavior of Ferritic Steel T22 Exposed to Supercritical Water
  56. A Multi Scale Strategy for Simulation of Microstructural Evolutions in Friction Stir Welding of Duplex Titanium Alloy
  57. Partition Behavior of Alloying Elements in Nickel-Based Alloys and Their Activity Interaction Parameters and Infinite Dilution Activity Coefficients
  58. Influence of Heating on Tensile Physical-Mechanical Properties of Granite
  59. Comparison of Al-Zn-Mg Alloy P-MIG Welded Joints Filled with Different Wires
  60. Microstructure and Mechanical Properties of Thick Plate Friction Stir Welds for 6082-T6 Aluminum Alloy
  61. Research Article
  62. Kinetics of oxide scale growth on a (Ti, Mo)5Si3 based oxidation resistant Mo-Ti-Si alloy at 900-1300∘C
  63. Calorimetric study on Bi-Cu-Sn alloys
  64. Mineralogical Phase of Slag and Its Effect on Dephosphorization during Converter Steelmaking Using Slag-Remaining Technology
  65. Controllability of joint integrity and mechanical properties of friction stir welded 6061-T6 aluminum and AZ31B magnesium alloys based on stationary shoulder
  66. Cellular Automaton Modeling of Phase Transformation of U-Nb Alloys during Solidification and Consequent Cooling Process
  67. The effect of MgTiO3Adding on Inclusion Characteristics
  68. Cutting performance of a functionally graded cemented carbide tool prepared by microwave heating and nitriding sintering
  69. Creep behaviour and life assessment of a cast nickel – base superalloy MAR – M247
  70. Failure mechanism and acoustic emission signal characteristics of coatings under the condition of impact indentation
  71. Reducing Surface Cracks and Improving Cleanliness of H-Beam Blanks in Continuous Casting — Improving continuous casting of H-beam blanks
  72. Rhodium influence on the microstructure and oxidation behaviour of aluminide coatings deposited on pure nickel and nickel based superalloy
  73. The effect of Nb content on precipitates, microstructure and texture of grain oriented silicon steel
  74. Effect of Arc Power on the Wear and High-temperature Oxidation Resistances of Plasma-Sprayed Fe-based Amorphous Coatings
  75. Short Communication
  76. Novel Combined Feeding Approach to Produce Quality Al6061 Composites for Heat Sinks
  77. Research Article
  78. Micromorphology change and microstructure of Cu-P based amorphous filler during heating process
  79. Controlling residual stress and distortion of friction stir welding joint by external stationary shoulder
  80. Research on the ingot shrinkage in the electroslag remelting withdrawal process for 9Cr3Mo roller
  81. Production of Mo2NiB2 Based Hard Alloys by Self-Propagating High-Temperature Synthesis
  82. The Morphology Analysis of Plasma-Sprayed Cast Iron Splats at Different Substrate Temperatures via Fractal Dimension and Circularity Methods
  83. A Comparative Study on Johnson–Cook, Modified Johnson–Cook, Modified Zerilli–Armstrong and Arrhenius-Type Constitutive Models to Predict Hot Deformation Behavior of TA2
  84. Dynamic absorption efficiency of paracetamol powder in microwave drying
  85. Preparation and Properties of Blast Furnace Slag Glass Ceramics Containing Cr2O3
  86. Influence of unburned pulverized coal on gasification reaction of coke in blast furnace
  87. Effect of PWHT Conditions on Toughness and Creep Rupture Strength in Modified 9Cr-1Mo Steel Welds
  88. Role of B2O3 on structure and shear-thinning property in CaO–SiO2–Na2O-based mold fluxes
  89. Effect of Acid Slag Treatment on the Inclusions in GCr15 Bearing Steel
  90. Recovery of Iron and Zinc from Blast Furnace Dust Using Iron-Bath Reduction
  91. Phase Analysis and Microstructural Investigations of Ce2Zr2O7 for High-Temperature Coatings on Ni-Base Superalloy Substrates
  92. Combustion Characteristics and Kinetics Study of Pulverized Coal and Semi-Coke
  93. Mechanical and Electrochemical Characterization of Supersolidus Sintered Austenitic Stainless Steel (316 L)
  94. Synthesis and characterization of Cu doped chromium oxide (Cr2O3) thin films
  95. Ladle Nozzle Clogging during casting of Silicon-Steel
  96. Thermodynamics and Industrial Trial on Increasing the Carbon Content at the BOF Endpoint to Produce Ultra-Low Carbon IF Steel by BOF-RH-CSP Process
  97. Research Article
  98. Effect of Boundary Conditions on Residual Stresses and Distortion in 316 Stainless Steel Butt Welded Plate
  99. Numerical Analysis on Effect of Additional Gas Injection on Characteristics around Raceway in Melter Gasifier
  100. Variation on thermal damage rate of granite specimen with thermal cycle treatment
  101. Effects of Fluoride and Sulphate Mineralizers on the Properties of Reconstructed Steel Slag
  102. Effect of Basicity on Precipitation of Spinel Crystals in a CaO-SiO2-MgO-Cr2O3-FeO System
  103. Review Article
  104. Exploitation of Mold Flux for the Ti-bearing Welding Wire Steel ER80-G
  105. Research Article
  106. Furnace heat prediction and control model and its application to large blast furnace
  107. Effects of Different Solid Solution Temperatures on Microstructure and Mechanical Properties of the AA7075 Alloy After T6 Heat Treatment
  108. Study of the Viscosity of a La2O3-SiO2-FeO Slag System
  109. Tensile Deformation and Work Hardening Behaviour of AISI 431 Martensitic Stainless Steel at Elevated Temperatures
  110. The Effectiveness of Reinforcement and Processing on Mechanical Properties, Wear Behavior and Damping Response of Aluminum Matrix Composites
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