Design of ESR Slag for Remelting 9CrMoCoB Steel under Simple Protective Ar Gas

Abstract

Thermodynamic calculations by using Factsage 7.3 and simple protective gas electroslag remelting (ESR) experiments were conducted to design the appropriate ESR slag for remelting the qualified 9CrMoCoB ingot. First, the proper basic slag was determined based on the phase diagram of CaF₂–CaO–Al₂O₃–x%MgO calculated using Factsage 7.3. Second, equilibrium reactions between 9CrMoCoB and the basic slag containing varied SiO₂, and B₂O₃ contents were calculated to study the effects of B₂O₃ and SiO₂ on B, Si, and Al contents in steel. Then, equilibrium reaction experiments were conducted to validate the calculated results. Finally, the appropriate slags were attained and the simple protective Ar gas ESR experiments were conducted to make a verification. Results showed that the liquid phase region of the slag of CaF₂–CaO–Al₂O₃–x%MgO at 1300–1400 °C increased first, then decreased with the MgO addition. With the B₂O₃ content increasing, the boron content increased, while the Si, Al contents decreased, and at a given B₂O₃ addition, the B and Al contents decreased with the SiO₂ content increasing, whereas the Si content increased. The appropriate slags for simple protective gas ESR remelting 9CrMoCoB were 55%CaF₂–20%CaO–3%MgO–22%Al₂O₃–2%SiO₂–1.3%B₂O₃ and 55%CaF₂–20%CaO–3%MgO–22%Al₂O₃–3%SiO₂–1.7%B₂O₃.

1. Introduction

Fossil fuel power plants currently supply more than 60% of the world’s electricity production, and they remain the most important sources of electricity in the near future [1,2]. To overcome the challenges of great energy consumption and high pollution associated with the fossil fuel power plants, improving the efficiency of thermal power plants by increasing the temperature and pressure of the working stream has been pursued for many decades. 9CrMoCoB (COST-FB2) was developed in the framework of European COST program for the production of large-scale rotor forging with good creep property at 625 °C and 32 MPa pressure. Under these ultra-supercritical conditions, the efficiency of thermal power plants can increase by ~5%, and CO₂ emissions can reduce by ~10%, compared with the world average at present [3,4].

The rotor is one of the most important components of steam turbines and its working condition is severe. Given that, high metallurgical quality is required. To reduce the loss of the chemically active and main reinforced elements B (the content rang of B is narrow: 0.008–0.011%) and produce the qualified ingot, many turbine manufacturers have adopted the protective Ar gas ESR [5,6] to produce the 9CrMoCoB ingot. However, the protective gas ESR furnance is costly and during the protective Ar gas ESR process, the soft arcing caused by the ionization of the argon has a bad effect on interior and exterior quality of the ingot [7]. To improve the ingot quality and reduce manufacturing cost, it is necessary to develop the proper slag for remelting the qualified ingot under the simple protective Ar gas.

The molten slag has a great influence on the metallurgical quality of the ingot during ESR process [8,9]. Previous researchers have extensively studied the effects of slag compositions and properties on the quality of the ingot. Pateisky [10], Medina [11], and Carmona [12] mainly researched the effects of slag compositions on the ingot contents during ESR process, and pointed out that to reduce the loss of the chemically active element, adding the components involved in the redox reaction into the molten slag is an effective method [13]. During the ESR process, if the redox reactions between the slag and steel are in equilibrium state, the contents of the chemically active alloyed elements in the ingot may keep steady.

Factsage is a useful tool for thermodynamic modeling of high-temperature metallurgical processes. Many researchers have adopted Factsage to simulate different ironmaking processes [14,15] and calculate the chemical physical properties of the slags [16]. In this work, the effects of the slag with varied SiO₂ and B₂O₃ contents on the B, Si, and Al contents in steel were studied via Factsage 7.3 calculations. Based on the calculated results, four slags were designed and the equilibrium reaction experiments were conducted to validate the calculated results. Then, the appropriate slags were attained by comprehensive analysis the calculated and experimental results, and the laboratory-scale simple protective gas ESR experiments were carried out to make a verification. The results of this work will provide some reference and guidance for the industrial production of the qualified 9CrMoCoB ingot using the simple protective Ar gas ESR.

2. Experiments and Calculations

The ESR slag compositions mainly include CaF₂, CaO, and Al₂O₃. A small amount of MgO is needed for reducing the electrical conductivity [17] and surface tension [18] of the molten slag.

The B (0.008–0.011%) and Al (0.003%) contents in the 9CrMoCoB are low, the Si (0.05%) content is relatively high, whereas the Al₂O₃ content in the ESR slag is high and the SiO₂ content is relatively low. The components involved in the redox reactions between the molten slag and steel are not in the standard state, and the ∆G of the reactions are related to the activities of the components. Thus, during ESR remelting 9CrMoCoB, reactions (1) and (2) may occur between molten slag and steel:

$${3\mathrm{Si}+2\mathrm{Al}}_2{\mathrm{O}}_3{=4\mathrm{Al}+3\mathrm{SiO}}_2$$

(1)

$${3\mathrm{Si}+2\mathrm{B}}_2{\mathrm{O}}_3{=4\mathrm{B}+3\mathrm{SiO}}_2$$

(2)

To reduce the loss of main reinforced element B and the accumulation of deleterious element Al, SiO₂ and B₂O₃ should be added into the slag to decrease the degree of slag–metal reactions [19]. To study the effects of B₂O₃ and SiO₂ addition into the molten slag on the B, Si, and Al contents in the steel, the compositions of the basic slag of CaF₂–CaO–Al₂O₃–MgO should be determined first.

2.1. Determining the Basic Slag

The liquidus temperature of 9CrMoCoB was 1498 °C calculated by using Thermo-Calc 6.4 (database TCFE7). The liquid phase region of CaF₂–CaO–Al₂O₃ with varied MgO addition at 1250–1400 °C with a 50 °C interval was calculated by using the Phase Diagram mode in Factsage 7.3 (database FToxid), results shown in Figure 1.

For the sake of reducing the energy consumption and the good surface quality of the ingot, the liquidus temperature of the molten slag should be lower than the liquidus temperature of the electrode by 100–200 °C [20], the proper liquidus temperature of the molten slag was 1300–1400 °C. In Figure 1, the area of the liquid phase region at 1300–1400 °C increased first, then, decreased, with the MgO addition. The liquid phase regions at 1300–1400 °C of the CaF₂–CaO–Al₂O₃ with 2%MgO or 3%MgO addition were both suitable for ESR process, and MgO addition can reduce the electrical conductivity and surface tension of the molten slag. Thus, in this work, 3%MgO addition was chosen.

The isothermal section phase diagram of CaF₂–CaO–Al₂O₃–3%MgO at 1200–1400 °C were calculated using the Phase Diagram mode in the Factsage 7.3 (database FToxid) and the calculated result is shown in Figure 2.

The CaF₂ content in ESR slag is usually ~50% to attain good fluidity. The slag compositions around the red dotted line (wt (Al₂O₃)/wt (CaO) = 1, shown in Figure 2) were usually chosen as the proper ESR slag for the relatively low liquidus temperature and stable chemical property [21]. During ESR process, the reaction between CaF₂ and CaO shown below led to the accumulation of CaO and loss of Al₂O₃.

$${3\mathrm{CaF}}_2{+\mathrm{Al}}_2{\mathrm{O}}_3{=2\mathrm{AlF}}_3+3\mathrm{CaO}$$

(3)

To keep the physical properties and the operation stable during the ESR process, wt (Al₂O₃)/wt (CaO) ratio should be slightly greater than 1. In this work, the designed proper basic slag was 55%CaF₂–20%CaO–22%Al₂O₃–3%MgO shown in Figure 2 (the red plot).

2.2. Factsage Calculations and the Equilibrium Reaction Experiments

2.2.1. Factsage Calculation

The equilibrium reactions between the molten 9CrMoCoB steel and the molten slag of 55%CaF₂–20%CaO–22%Al₂O₃–3%MgO–x%SiO₂–y%B₂O₃ were calculated by using Equilib mode in Factsage 7.3 (database FToxid, FTmisc, and FactPS) to figure out the effects of B₂O₃ and SiO₂ contents in the slag on the B, Si, and Al contents in steel. The calculated conditions follow; mass ratio of the slag with steel was 1:6, temperature was 1823 K (1550 °C), and atmosphere was 1 mol Ar with 0.0002 mol O₂ under 0.1 MPa (volume fraction of O₂ was 0.2%).

Based on the calculated results, four slags were designed. To verify the calculated results, the equilibrium reaction experiments between the designed slags and 9CrMoCoB steel were conducted using the four designed slags.

2.2.2. Equilibrium Reaction Experiments

The reagent-grade powders of wt (CaO) ≥ 97%, wt (MgO) ≥ 98%, wt (CaF₂) ≥ 98.5%, wt (Al₂O₃) ≥ 98.5%, wt (SiO₂) ≥ 98.5% and wt (B₂O₃) ≥ 98% were used to pre-melt the slags. The powders were mixed completely, then put in a graphite crucible lined with a 0.2 mm-thick molybdenum film and heated in the MoSi₂ furnace shown in Figure 3. During the experiment, the temperature was continuously measured using a B-type thermocouple, and the final temperature was 1723 K (1450 °C). For composition homogeneity, the slags were held at 1723 K for 50 min and then furnace-cooled to room temperature. The crushed pre-melted slags were subjected to chemical analysis. The B₂O₃ and SiO₂ contents were analyzed in the national analysis center for iron and steel (CISRI) using the method of ICP-AES, and the other main chemical compositions of the slags were analyzed using the X-ray fluorescence spectroscopy (Rigaku ZSX Primus II, Tokyo, Japan).

Each equilibrium reaction experiment was conducted with 600 g 9CrMoCoB steel (remelted in Electrometallurgy Laboratory of Northeastern University using the 30 kg vacuum induction furnace and contents shown in

Table 1. The compositions of 9CrMoCoB steel wt.%.

Content	C	Si	Mn	B	Al	Cr	Mo	Co	O	Ni	Nb	N	Fe
EXP.	0.136	0.0495	0.34	0.010	0.003	9.36	1.48	1.28	0.0028	0.16	0.06	0.021	Bal.
Min.	0.110	-	0.28	0.008	-	9.05	1.40	1.15	-	0.10	0.04	0.015
Max.	0.150	0.1000	0.42	0.011	0.01	9.60	1.60	1.45	0.0035	0.25	0.07	0.030
Goal	0.120	0.0500	0.35	0.010	0.007	9.30	1.50	1.30	-	0.15	0.06	0.020

) and 100 g pre-melted slag. The experiments were conducted in a magnesium oxide crucible lined with a 0.2-mm-thick molybdenum film at the isothermal zone of the MoSi₂ furnace shown in Figure 3. The furnace was heated to preset 1823 K (1550 °C) at a rate of 8 K/min. During the experiments, pure argon began to blow from gas tube into the furnace as the protecting gas when the temperature was above 673 K (400 °C). The bottom argon gas flow rate was 3 NL/min, and the top argon gas flow rate was 6 NL/min, the concentration of O₂ in the furnace atmosphere ranged from 0.2 to 0.3% (volume fraction).

When the temperature reached 1823 K, the −0# steel sample was taken as the initial steel chemical composition using a quartz tube. One-hundred grams of pre-melted slag was then put into the crucible divided into five times, and to avoid the slag to be out of the crucible, the crushed pre-melted slag was wrapped in paper. To determine the equilibrium time of the reactions, it is necessary to take samples at different reaction times. The reaction time began to calculate after the slag was added (the time for adding the slag was as short as 50 s, so the time was negligible). Subsequently, the steel samples were taken at 20, 40, and 60 min and labeled as −1#, −2#, and −3#, respectively. To extract the steel sample, the furnace lid should be lifted away from the furnace first, then the quartz tube was put into the furnace to extract the steel sample from the top of the furnace. The extracted steel samples were cooled in water immediately.

2.3. Laboratory-Scale ESR Experiments

2.3.1. The Viscosity of the Proper Slags

The proper slags were obtained based on the comprehensive analysis the experimental and calculated results. The viscosity of the proper slags was calculated by using Viscosity mode in Factsage 7.3. In the Viscosity mode in Factsage, the molten slag was assumed to be the single liquid phase at any temperature. The actual viscosity (viscosity of slag containing solid precipitations) was calculated using the equation of Einstein–Roscoe [22] shown in Equation (4).

$$\eta ={\eta }_0\ast {(1-\alpha f)}^{-n}$$

(4)

Here, η is the actual viscosity of the melt, η₀ is the calculated viscosity by Factsage 7.3, α and n are constants, and f is the volume fraction of the solid particles in the melt.

Roscoe suggested α and n to be 1.35 and 2.5 [23], respectively, by assuming that solid precipitation was spherical particles with a uniform size. To simplify the calculation, the mass fraction of the crystalline phase was instead of the volume fraction [24]. The mass of the precipitates during the solidification were calculated by using the Equilib mode in Factsage 7.3.

2.3.2. Laboratory-Scale Simple Protective Gas ESR Experiments

To produce the qualified ingot, the viscosity of the molten slag should change slightly with the temperature changing. Based on the analysis of the calculated viscosity of the slags, the appropriate slags were obtained. The laboratory-scale ESR experiments were conducted to make a verification. The compositions of the electrodes are shown in

Table 2. The compositions of electrode wt.%.

C	Si	Mn	B	Al	Cr	Mo	Co	O	Ni	Nb	N	Fe
0.132	0.048	0.348	0.0098	0.004	9.49	1.54	1.27	0.0028	0.15	0.058	0.024	Bal.

, and the detailed ESR operating parameters are shown in

Table 3. The detailed operating parameters of the laboratory-scale ESR.

ESR Melting	Furnace	Simple Protective Furnace
	Remelting speed/kg/min	1.2
Mould	Diameter/mm	125
Electrode	Diameter/mm	75
Slag	Weight/kg	3.2

. The ESR experiments were conducted under the simple protective gas, and the schematic diagram of the experimental set-up was shown in Figure 4. During the remelting process, pure Ar was blown at 24 NL/min. An oxygen concentration sensor was used to detect the concentration of O₂ above the molten slag to adjust the concentration of O₂ at 0.5% (volume fraction, the lower limit of the furnace).

To analyze the vertical distributions of B, Si, and Al contents in the ESR ingot from bottom to top, the ingot was vertically cut into two parts through its center and the procedures were shown in Figure 5. The analysis mainly focused on vertical changes of B, Si, and Al contents from bottom to top of the ingot.

2.4. Analysis

An optical emission spectrometer (ARL 4460, Waltham, MA, USA) was used to detect the main alloying elements in the steel samples. The alloyed elements B, Al, and Si contents were analyzed in the national analysis center for iron and steel (CISRI) using the method of ICP-AES.

3. Results and Discussions

3.1. Calculated Results by Using Factsage 7.3

The calculated results of the equilibrium reactions between molten slag of 55%CaF₂–20%CaO–3%MgO–22%Al₂O₃–x%SiO₂–y%B₂O₃ (x ≤ 3, y ≤ 3) and 9CrMoCoB using Factsage 7.3 are shown in Figure 6. In Figure 6, the B, Si, and Al contents were the equilibrium contents in the molten steel after reaction with the molten slag with varied SiO₂ and B₂O₃ contents.

As shown in Figure 6, the boron content increased, while the Si, Al contents decreased simultaneously with the increasing B₂O₃ addition. Further, at a given B₂O₃ addition, the B, Al contents decreased, while the Si content increased concurrently with the increasing SiO₂ addition. The range of the B content was also shown in Figure 6. The red dotted line was the upper limit of the B content range (0.011%), the blue dotted line was the lower limit of the B content range (0.008%). To verify the calculated results, the four designed slags are shown in

Table 4. The compositions of the new designed slag wt.%.

	Before Pre-Melted						After Pre-Melted
NO.	CaF2	CaO	Al2O3	MgO	SiO2	B2O3	CaF2	CaO	Al2O3	MgO	SiO2	B2O3
1#	55	20	22	3.0	0.0	0.5	52.90	21.15	21.71	3.08	0.18	0.47
2#	55	20	22	3.0	1.0	1.0	52.60	20.56	21.46	3.03	1.16	0.96
3#	55	20	22	3.0	2.0	1.3	51.96	20.22	21.19	2.98	2.11	1.24
4#	55	20	22	3.0	3.0	1.7	51.32	20.03	20.91	2.95	3.05	1.61

. The compositions of the pre-melted slags are also shown in Table 4.

3.2. Results of Equilibrium Reaction Experiments

The changes in B, Si, and Al contents in the steel versus time of the four equilibrium reaction experiments using the designed slags are shown in Figure 7. The B, Si, and Al contents at different reaction time were not the equilibrium contents in the molten steel. Thus, the Al content changing with time behavior was not the same with the behavior of Al changing with the B₂O₃ addition shown in Figure 6.

As seen in Figure 7a, the boron content in the 2#~4# heats kept steady, whereas in the 1# heat, the boron content decreased slightly at first, then kept steady soon. In Figure 7b, the Si content in 1# heat decreased distinctly, and reached stable after 40 min, whereas in 2#~4# heats, the Si content decreased slightly, then kept steady soon. In Figure 7c, the Al content increased with the reaction time, and the Al content reached stable after 40 min in the four heats. In the equilibrium reaction experiments, the reaction between Si and Al₂O₃ was not in equilibrium state, the Al content changed compared to the initial content. These results indicated that the reactions between slag and steel were in equilibrium state at 60 min.

The equilibrium B, Si, and Al contents calculated by using Factsage were compared with the experimental equilibrium B, Si, and Al contents at 60 min, and the results are shown in Figure 7d.

In Figure 7d, the calculated equilibrium B, Si, and Al contents were close to the experimental results. In the 2# heat, the B content kept steady, and the Si content decreased slightly with the reaction time. Thus, the reaction between Si and B₂O₃ was in equilibrium state during the experiments. The Al content increased with the reaction time, but the consumption of Si caused by the reaction between Si and Al₂O₃ was very limited, so the loss of Si was not only caused by the reaction between Si and Al₂O₃. The equilibrium reaction experiment was not conducted in the fully sealed furnace, atmospheric oxygen can enter in the furnace, and the reaction between Si and FeO (oxidation products during the melting process) occurred led to the loss of Si. With the SiO₂ content in the slag increasing, the reaction between the Si and FeO was annihilated and the deviation of Si content between the experimental and calculated results became small. Thus, in the 1# heat, the Si content in the experimental results was a little less than the Si content in the calculated results can be understandable. On the whole, the calculated results by Factsage were similar to the experimental results.

From the above analysis, the 1# slag was not suitable for ESR remelting 9CrMoCoB steel, for the equilibrium Al content (0.0076%) was close to the upper limit (0.01%), and the loss of Si content was great in the equilibrium reaction experiment using the 1# slag. While in the equilibrium reaction experiments using the 2#~4# slags, the loss of the equilibrium content of Si and the increasement of the equilibrium content of Al was slight, and the equilibrium B, Si, and Al contents kept steady soon. The redox reactions between the molten slag and steel were in quasi-equilibrium state, thus the proper slag for ESR remelting 9CrMoCoB ingot were the 2#, 3#, and 4# slags [10,19].

3.3. The Viscosity of the Proper Slags

The mass of the precipitates during the solidification were calculated by using the Equilib mode in Factsage 7.3 (database melts) and the calculated results are shown in Figure 8.

In Figure 8, the total mass of crystallization phase of CaF₂ generally kept steady for the three slags. The total mass of crystallization phases of MgAl₂O₄, Ca₃B₂O₆, and Ca₁₁B₂Si₄O₂₂ increased, whereas the total mass of crystallization phases of Ca₁₂Al₁₄F₂O₃₂ and MgO decreased with the increasing B₂O₃ and SiO₂ addition. The MgO did not precipitate in the 4# slag.

According to the calculated results by using the Equilib and Viscosity modes in Factsage 7.3, the calculated modified viscosity of the proper slags versus temperature using Equation (4) are shown in Figure 9.

In Figure 9, when the temperature ≥ 1300 °C the viscosity of the three proper slags were similar, and the viscosity changed slightly with temperature changing, which was beneficial to attain the good surface quality of ingot during ESR process.

3.4. Laboratory-Scale ESR Experiments

The viscosity of the three proper slags were all suitable for ESR remelting 9CrMoCoB ingot, and the ingots remelted under the simple protective gas using the 2#, 3#, and 4# slag are shown in Figure 10a–c, respectively. The surface quality of the three ingots was good. During the ESR process, the concentration of O₂ ranged from 0.4% to 0.6% (volume fraction).

The vertical distributions of B, Si, and Al contents in the three ESR ingots are shown in Figure 11, respectively.

As shown in Figure 11, the B content in the ingots remelted using the 2# and 3# slags was ~0.01%, whereas the B content in the ingot remelted using the 4# slag was ~0.0095% with a slight loss. The Al content (≤ 0.006%) in the ingots remelted using the 2#~4# slags kept steady and all was within the target range. The Si content in the ingot remelted using the 2# slag decreased first, and then became steady at ~0.022%. The loss of Si in the ingot remelted using the 2# slag maybe caused by the reaction between Si and the oxidation products of FeO during the remelting process. During the laboratory-scale ESR process, the oxygen in the atmosphere permeated into the molten slag pool or the electrode was oxidized by the O₂ in the atmosphere, which increased the FeO content in the molten slag pool. The Si content in the ingots remelted using the 3# slag and 4# slag decreased first, then quickly kept steady around 0.036% and 0.038%, respectively (the SiO₂ content in the molten slag pool was relatively high, the reaction between Si and FeO was inhibited).

According to the laboratory-scale ESR experiments, the B, Si, and Al contents were all within the target range, but the loss and the macro-segregation of Si in the ingot remelted using the 2# slag was obvious; therefore, the 2# slag was not suitable for ESR remelting 9CrMoCoB steel under the laboratory-scale ESR experiment conditions. The Si content decreased in the ingots remelted using the 3# and 4# slags first, but the Si content kept steady soon.

The appropriate slags for ESR remelting 9CrMoCoB steel were the 3# slag of 55%CaF₂–20%CaO–22%Al₂O₃–3%MgO–2%SiO₂–1.3%B₂O₃ and the 4# slag of 55%CaF₂–20%CaO–22%Al₂O₃–3%MgO–3%SiO–1.7%B₂O₃ under the simple protective Ar gas.

4. Conclusions

The principal conclusions conducted from this study are summarized as follows.

(1)

The liquid phase region of CaF₂–CaO–Al₂O₃–x%MgO (0≤ x ≤5) at 1300~1400 °C with the MgO addition, increased first, then, decreased.

(2)

With the increasing B₂O₃ content, the equilibrium boron content increased, whereas the equilibrium Si, Al contents decreased simultaneously, and, at a given B₂O₃ addition, the equilibrium B, Al contents decreased, whereas the equilibrium Si content increased concurrently with increasing SiO₂ content.

(3)

On the whole, the Factsage calculation results were similar to the experimental results under the same experimental conditions.

(4)

The designed slags of 55%CaF₂–20%CaO–22%Al₂O₃–3%MgO–0%SiO₂–0.5%B₂O₃ and 55%CaF₂–20%CaO–22%Al₂O₃–3%MgO–1%SiO₂–1%B₂O₃ were not suitable for remelting qualified 9CrMoCoB ingot for the obvious loss and macro-segregation of Si.

(5)

The slags of 55%CaF₂–20%CaO–22%Al₂O₃–3%MgO–2%SiO₂–1.3%B₂O₃ and 55%CaF₂–20%CaO–22%Al₂O₃–3%MgO–3%SiO₂–1.7%B₂O₃ were appropriate for ESR remelting qualified 9CrMoCoB ingot under the simple protective Ar gas (volume fraction of O₂ was around 0.5%) with controlling the B, Si, and Al contents within the target range and avoiding the macrosegregation of Si.