Residual Stress Differences between Uniform and Non-Uniform Heating Treatment of Bimetallic Roll: Effect of Creep Behavior on Residual Stress

Abstract

The work roll is one of the most important tools in the steel rolling industry. Work rolls are used under extremely severe conditions such as high temperature, high loading, and an aggressive atmosphere. To meet those demands, bimetallic rolls have recently been used to replace conventional single material rolls. Usually, a compressive residual stress is introduced to prevent surface cracking. However, a tensile residual stress at the center appears to balance the compressive residual stress. This center residual stress sometimes causes roll failure. In this paper, therefore, a simulation is performed using the finite element method (FEM) for the quenching process of the bimetallic roll by considering the creep behavior. Then the effect of pre-heating conditions is discussed. The results show that the maximum stress point for the tensile stress at the roll center for non-uniform heating is 24% less than that achieved with uniform heating, although the same compressive stresses appear at the surface. Then, using different work roll diameters, the center tensile residual stress for non-uniform heating is found to be smaller than the uniform heating. Also, it is found that the area ratios of the shell-core only have a small influence on the residual stress of the bimetallic roll for both heating treatments.

1. Introduction

In order to improve work roll performance in steel rolling industries, many studies have been conducted to investigate wear resistance, surface roughness, and center toughness [1,2,3,4]. To meet such different demands, bimetallic rolls, as shown in Figure 1, have been widely used to replace the conventional single material rolls [5]. Bimetallic rolls are manufactured by the centrifugal casting method, in which high-speed steel (HSS) is used as the shell and ductile casting iron (DCI) is used as the core (see Figure 1) [6,7,8].

Figure 1. Model of the bimetallic roll (mm).

Quenching heat treatment produces compressive residual stress to prevent fatigue crack at the roll outer layer [9,10,11,12]. However, to balance the compressive stress, tensile residual stress always appears at the roll center, which may cause roll fracture. Decreasing the center tensile stress is therefore desirable to reduce the risk of fracture from the roll center. Since the residual stress can be controlled by the heat treatment, an appropriate quenching process is required to improve bimetallic roll quality [13,14,15,16].

In our previous study [17,18,19], the usefulness of non-uniform heating treatments was explained, although the material data were not indicated at the request of the company with which we collaborated. Since the material data could not be indicated, the detailed effect of the material on the residual stress has not yet been clarified. Therefore, in this paper, the simulation will be performed under specific material data where the new materials and new roll are considered. Then, the effect of the heat treatment will be discussed clearly by applying the finite element method (FEM) to the quenching process after uniform heating and non-uniform heating. Moreover, the effects of the roll diameter and the area ratio on the residual stresses will be discussed.

2. Mechanical Properties and Materials Data of Bimetallic Roll

As shown in Figure 1, we assumed a composite roll with a diameter of 660 mm, outer layer thickness of 60 mm, and body length of 1800 mm. In order to remove the internal stress caused by the transformation in the cooling process after casting, the roll was annealed and gradually cooled to room temperature. As a result, the residual stress was considered negligible before the heating treatment, which was held at a temperature exceeding 1000 °C. Even in the case of non-uniform heating, since the whole work roll was heated and then maintained at 600 °C or higher, stress-free conditions were set as the initial conditions of the analysis.

Figure 2 shows the microstructure of the outer and inner layers around the boundary layer. In the outer layer of HSS, the carbides are fine and homogeneously distributed but coarsened at the boundary. In the inner layer of DCI, the spherical graphite is surrounded by ferrite. In Figure 2, a good diffusion state is maintained at the boundary and good composite structures are seen. Table 1 shows the material properties for the outer layer of HSS and the inner layer of DCI. The outer layer HSS has a composition of Carbon (1–3%), Silicon (<2%), Manganese (<1.5%), Phosphorus (<1%), Sulphur (<1%), Nickel (<5%), Chromium (2–7%), Molybdenum (<10%), Cobalt (<10%), Vanadium (3–10%), Wolfram (<20%) and Magnesium (<10%). Meanwhile the inner DCI has a composition of Carbon (2.5–4%), Silicon (1.5–3.1%), Manganese (<1%), Phosphorus (<0.1%), Sulphur (<0.1%), Nickel (0.4–5%), Chromium (0.01–1.5%), Molybdenum (0.1–1%), Cobalt (<1%), Vanadium (<1%), Wolfram (<1%) and Magnesium (0.02–0.08%) in its composition.

Figure 2. View of microstructure for a high-speed-steel-type roll with a ductile core. *Reproduced with permission from Noda et al., Journal of the Japan Society for Technology of Plasticity, 2018.

Table 1. Mechanical properties of the shell and core at room temperature.

Property	Shell	Core
0.2% proof stress (MPa)	$1270$	410
Young’s modulus (GPa)	228	168
Poisson’s ratio	0.3	0.28
Density (kg/m3)	7600	7300
Thermal expansion coefficient (K−1)	12.6 × ${10}^{-6}$	13.0 × ${10}^{-6}$
Thermal conductivity (W/m·K)	20.2	23.4
Specific heat (J/(kg·K)	0.46	0.42
Shore hardness (Hs)	85	50

In our previous study [19], the material data were not indicated in detail since they constituted confidential information of the roll manufacturing company. Since the purpose of this study is to clarify the residual stress during the quenching process, all material data are provided, as shown in Figure 3. This figure shows the Young’s modulus, specific heat, thermal conductivity, thermal expansion coefficient, Poisson’s ratio, and stress-strain characteristic for both HSS and DCI during the quenching process.

Figure 3. (a) Young’s modulus; (b) specific heat; (c) thermal conductivity; (d) thermal expansion coefficient during quenching; (e) Poisson’s ratio; (f) stress-strain for HSS; (g) stress-strain for DCI.

3. FEM Modeling

For the FEM analysis, the software MSC Software’s Marc and Mentat 2012 was used to perform the simulation of the quenching process of the bimetallic roll, while the Newton-Raphson strategy was used to solve non-linear equations in an implicit scheme. Figure 4 shows the transient-static simulation model of a half-length of the roll by using a four-node linear axisymmetric quad element with a mesh size of 5 × 5 mm. Due to the symmetry, the thermal isolation conditions and displacement boundary conditions are applied to $\mathrm{z}=0$. This thermo-elastic plastic material model consists of 17,785 elements with 18,150 nodes and considered the Von Mises yield criterion and isotropic strain hardening rule.

Figure 4. Analytical model and boundary condition for bimetallic roll.

Figure 5 shows the temperature of the roll surface for (a) uniform heating; (b) non-uniform heating. All the material properties were measured experimentally from the initial quenching temperature, ${\mathrm{T}}_{\mathrm{Start}}$, to the end hardening temperature, ${\mathrm{T}}_{\mathrm{Finish}}$. These temperature histories are used as the thermal loading to create the residual stress field. Therefore, the thermal strains and stresses for each increment can be calculated.

Figure 5. Schematic diagram of surface temperature for (a) uniform heating; (b) non-uniform heating.

For uniform heating in Figure 5a, the entire work roll was heated up to the quenching start temperature, ${\mathrm{T}}_{\mathrm{Start}}$. Due to the uniform heating treatment, no residual stress appeared before the quenching process. For non-uniform heating in Figure 5b, the entire roll was heated up initially to the pre-quenching temperature, ${\mathrm{T}}_{\mathrm{Heating}}$. After maintaining this temperature, ${\mathrm{T}}_{\mathrm{Heating}}$, for a certain time, the roll was rapidly heated up to a higher temperature. Due to this kind of treatment, small residual stress that is less than 30 MPa was found at the early stage of the quenching process. When the surface temperature reached the starting temperature ${\mathrm{T}}_{\mathrm{Start}}$, a mixed of water and air was discharged from the furnace to start the cooling process. During the cooling, the surface temperature of the roll was maintained at the keep temperature, ${\mathrm{T}}_{\mathrm{Keep}1}$, to alleviate the thermal stress accompanying the rapid decrease of the surface temperature. Then, the roll was cooled down slowly to the end temperature, ${\mathrm{T}}_{\mathrm{Finish}}$. The stress at this point was treated as the residual stress in this study, although the tempering was not completed. In the tempering treatment, the roll was tempered in the furnace after being heated up to the keeping temperature, ${\mathrm{T}}_{\mathrm{Tempering}}$, and maintained for a certain time. Then, it was gradually cooled in the furnace to complete the heat treatment.

In the creep analysis, the transient creep strain was considered where the time hardening law was used to express the core material due to its low strength under high temperature. The core creep equation is given as:

$${\epsilon }_c=A{\sigma }^m{t}^n$$

(1)

where ${\epsilon }_c$ is the transient strain, $\sigma$ is the stress, $t$ is the time, and A, m, and n are temperature-dependent material constants. All these unknown constants are determined by performing experimental creep tests [19]. Since the formula was used under constant temperature in the present simulation, this expression of the creep strain depended only on time and stress.

4. Influence on Residual Stress by Non-Uniform Heating

By performing non-uniform heating, the surface and center temperatures will be different. As a result, the risk of roll failure can be reduced by decreasing the center tensile residual stress. The other advantages of non-uniform heating quenching are listed as follows:

• The internal temperature is lower than 900 °C, which contributes to the avoidance of overheating and prevents material deterioration.
• Due to the rapid cooling of the quenching, a hard shell is obtained, improving the impact strength of the roll.
• Energy consumption can be reduced because the heating time is shortened.
• The time and cost of the operation can be also reduced since the time required for heating is shortened.

Figure 6 shows the distribution of the residual stress ${\sigma }_z$ in the central cross-section of the roll. In this thermal analysis, a total of 905 load steps, corresponding to $t=1140 \mathrm{s}$, were required to complete the heating cycles.

Figure 6. Comparison of residual stress distribution, ${\sigma }_z$, for both heating treatments.

As shown in Figure 6, the maximum tensile stress for non-uniform heating appearing at the roll center decreased to as low as 141 MPa. The compressive residual stress at the surface decreased, but remained sufficiently large enough to guard against thermal crack. Meanwhile, the maximum tensile stress for non-uniform heating was 24% less than that for uniform heating. From Figure 6, it may be considered that non-uniform heating is efficient in reducing the fracture risk at the roll center without losing the crack prevention ability of the roll surface.

5. Comparison between Uniform Heating and Non-Uniform Heating

5.1. Stress Generation Mechanism of Uniform Heating and Non-Uniform Heating

Figure 7 and Figure 8 show the results for (a) temperature versus time and (b) corresponding stress, ${\mathsf{\sigma }}_{\mathrm{z}}$, versus time for uniform and non-uniform heating processes, respectively.

Figure 7. Uniform heating process and corresponding stress, ${\sigma }_z$: (a) temperature at the center and surface; (b) stress,${\sigma }_z$, at the center and surface.

Figure 8. Non-uniform heating process and corresponding stress, ${\sigma }_z$: (a) temperature at the center and surface; (b) stress,${\sigma }_z$, at the center and surface.

As shown in Figure 7, the period Ⓐ is a heating process while the periods Ⓑ, Ⓒ, Ⓓ, and Ⓔ are the quenching processes. During process Ⓐ, no difference can be seen between the center and surface since the roll is heated up uniformly and no stress occurs. During the rapid surface cooling process Ⓑ, the tensile stress of the outer layer increases initially due to the cooling shrinkage of the outer layer. However, the tensile stress suddenly changes to compressive stress because the thermal shrinkage at the central part becomes larger. Pearlite transformation appears at the inner layer at the pearlitization temperature, ${\mathrm{T}}_{\mathrm{Pearlite}}$, which expands from the inner layer boundary toward the roll center. During this process, Ⓑ, the center compressive stress decreases until reaching ${\mathrm{T}}_{\mathrm{Pearlite}}$. During process Ⓒ, the pearlite transformation causes the formation of compressive stress at the roll center. Then, the tensile stress at the center with a high cooling rate increases and eventually the stress at the center and the stress at the surface intersect. The compressive stress at the surface and the tensile stress at the center maintain until the temperature ${\mathrm{T}}_{\mathrm{Keep}2}$ is reached. During the initial temperature keeping period, Ⓓ, since the heating is applied to adjust the overcooling at the roll surface, both the surface compressive stress and the center tensile stress increase slightly. After heating, the temperature difference becomes smaller between the surface and the center. During period Ⓔ, the surface cooling starts outside the furnace, and the surface temperature decreases. Then, the center tensile stress and the surface compressive stress both increase. During period Ⓔ, Bainite expansion transformation occurs at the inner layer at the bainitization temperature, ${\mathrm{T}}_{\mathrm{Bainite}}$, promoting the surface compressive stress and the center tensile stress.

As shown in Figure 8, during the non-uniform heating process, Ⓐ, the entire roll is heated up initially to the pre-quenching temperature, ${\mathrm{T}}_{\mathrm{Heating}}$. After that, the roll surface is rapidly heated up to the roll surface temperature, ${\mathrm{T}}_{\mathrm{Start}}$, while the roll center is heated at a lower temperature in a non-uniform manner. At the early stage of this heating process, tension is generated at the center due to the surface thermal expansion. The surface compressive stress turns into tensile stress due to transformation contraction at the austenitization temperature, ${\mathrm{T}}_{\mathrm{Austenite}}$. After that, the temperature difference becomes smaller between the surface and the center and both stresses decrease. At the initial stage of quenching, Ⓑ, a large tensile stress forms at the surface because of the high cooling speed. The pearlite transformation occurs at the initial stage of Ⓒ, and the center compressive stress is maintained. At the initial stage of Ⓓ, due to the roll surface heating process, the surface tensile stress turns into compressive stress. During the temperature keeping period, ${\mathrm{T}}_{\mathrm{Keep}1}$, the temperature difference becomes smaller between the surface and the center. Then, the stress change is small. During the air-cooling period, Ⓔ, Bainite expansion transformation occurs. In the outer layer—similar to the uniform heating case in Figure 7—both the surface compressive stress and the center tensile stress increase.

As shown in Figure 6, the central compressive stress under uniform heating becomes smaller than that under non-uniform heating. This can be explained by the following. During pearlite transformation, ⓟ, in Figure 7 and Figure 8, the stress change under non-uniform heating (indicated as ⓟ in Figure 8) is smaller than the stress change under uniform heating (indicated as ⓟ in Figure 7). In a similar way, the central stress increase (indicated as ⓣ in Figure 8) under non-uniform heating is also smaller than the central stress increase (indicated as ⓣ in Figure 7) under uniform heating after the pearlite transformation. The effects of the temperature keeping period, Ⓓ, and air-cooling period, Ⓔ, are nearly the same in Figure 7b and Figure 8b. In the non-uniform heating process, the smaller stress increase after the central pearlite transformation results in the reduction of the center tensile stress.

5.2. Effect of Diameter on Uniform Heating and Non-Uniform Heating

Figure 9a shows the residual stress distribution for uniform heating obtained by varying the diameter from 500 mm to 1000 mm in increments of 100 mm with an area ratio of 0.4. Since the area ratio is fixed, the residual stress of the inner layer can be represented by the stress at the center. At the center, the tensile stress increases by 53 MPa as the diameter changes from 500 mm to 1000 mm. Meanwhile, Figure 9b shows the diameter effect result of non-uniform heating. The result is significant as the real roll diameter used is between 600 mm to 800 mm. The maximum tensile stress at the inner layer is 261 MPa when the roll diameter is 900 mm. The surface compressive stress varies significantly as the roll diameter changes from 500 mm to 600 mm.

Figure 9. Residual stress distribution, ${\sigma }_z$, for different diameters. (a) Uniform heating; (b) non-uniform heating.

5.3. Effect of Area Ratio on Uniform Heating and Non-Uniform Heating

Figure 10a,b shows the residual stress distribution for different area ratios for uniform and non-uniform heating processes, respectively. The outer roll diameter is fixed as 660 mm. For uniform heating, the center tensile stress increases by 120 MPa as the area ratio changes from 0.2 to 0.8. Meanwhile, for non-uniform heating, the tensile stress increases by 127 MPa for the same ratios. The compressive stresses at the surface are almost unchanged for both results. The results show that the area ratio only exerts a small influence on the residual stress of the bimetallic roll.

Figure 10. Residual stress distribution, ${\sigma }_z$, for different area ratios. (a) Uniform heating; (b) non-uniform heating.

6. Conclusions

In this study, residual stress was discussed under uniform and non-uniform heating treatments by considering creep behavior. The bimetallic roll tested consisted of high-speed steel at the shell and ductile cast iron at the core. Although a similar study can be found in previous work, no material data was indicated. In the current work, all the material data were indicated to provide a detailed view of the effects of material properties on residual stress.

After uniform and non-uniform heating treatments, the quenching process was simulated by applying thermo-elastic plastic finite element method analysis. The conclusions are summarized as follows:

• The tensile stress of the inner layer after non-uniform heating and quenching was less than that obtained after uniform heating and quenching by 24%, while the compressive stress on the surface for both heating treatments did not differ greatly. As a result, the effect of preventing surface cracking can be expected to reduce damage originating from the center.
• Based on the stress generation mechanisms, it was found that the stress in the central part decreased by non-uniform heating because during pearlite transformation, Ⓑ, the increase in the central stress in non-uniform heating (ⓟ) was small. Similarly, the increase in the central stress (ⓣ) in non-uniform heating is also small in region Ⓒ after the pearlite transformation.
• Based on the diameter effect result, the center tensile stress for non-uniform heating was smaller compared to that for uniform heating. Furthermore, the surface compressive stress varied significantly as the diameter changes from 500 mm to 1000 mm.
• The results of the area ratio effect showed that the center tensile stress for non-uniform heating was smaller than that for uniform heating, while the compressive stress at the surface was almost unchanged for both results. In conclusion, the area ratio only exerts a small influence on the residual stress of bimetallic rolls for both heating treatments.