Hot Deformation Behavior and Processing Maps for a Large Marine Crankshaft S34MnV Steel

Chen, Zhiying; Nash, Philip

doi:10.1002/srin.201700321

Cited by 11 publications

(5 citation statements)

References 34 publications

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“…By substituting the previous results into Equation (4), the hot deformation equation of the test steel under the deformation at 850–1200 °C and 0.01–10 s −1 can be obtained as follows:

\begin{array}{c}\stackrel{\cdot }{\epsilon }=1.33\times {10}^{15}[\text{sin}h(0.0081\sigma ){]}^{5.96}\text{exp}(-380486/\mathit{\text{R}}T)\end{array}

Table 3 shows the n , α , and Q values for S34MnV and 30CrMnSiNi2A steel, which are both high‐strength low‐alloy steels. [ 26,39 ] For 30CrMnSiNi2A steel, Q increases with increasing contents of carbon and alloying elements contents, as evidenced by the increase in the temperature dependence of the flow stress. For S34MnV and 30CrMnSiNi2A steels, n ranged from 4 to 5.…”

Section: Resultsmentioning

confidence: 99%

“…It is most widely used to describe the relationship between the strain rate, flow stress, and temperature, especially at high temperatures. [ 23 ] Processing maps based on the dynamic material model (DMM) theory [ 26 ] were constructed to design and optimize the materials hot working processes for the materials.…”

Section: Methodsmentioning

confidence: 99%

“…Table 3 shows the n, α, and Q values for S34MnV and 30CrMnSiNi2A steel, which are both high-strength low-alloy steels. [26,39] For 30CrMnSiNi2A steel, Q increases with increasing contents of carbon and alloying elements contents, as evidenced by the increase in the temperature dependence of the flow stress. For S34MnV and 30CrMnSiNi2A steels, n ranged from 4 to 5.…”

Section: Constitutive Equation For Hot Deformationmentioning

confidence: 97%

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Hot Deformation Behavior of a Marine Engineering Steel for Novel 980 MPa Grade Extra‐Thick Plate

Wang,

Ren,

Liu

et al. 2024

steel research int.

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The hot deformation behavior of a marine engineering steel for a novel 980 MPa grade extra‐thick plate is investigated through hot compression tests at temperatures of 850–1200 °C and strain rates of 0.01–10 s−1. The flow stress curves are corrected to eliminate the effects of friction on the flow stress, and a modified constitutive model is established to accurately quantify the flow behaviors of the steel. Hot working maps of the steel are derived by using a dynamic materials model and the Prasad instability criterion. The effects of the deformation parameters on the dynamic recrystallization (DRX) nucleation mechanisms are evaluated using scanning electron microscopy and electron backscatter diffraction. The flow stress and peak strain increased with decreasing deformation temperature and increasing strain rate, respectively. The activation energy for hot deformation after friction correction is 380.49 kJ mol−1. The DRX mechanism involves the migration of subgrains. The deformation parameters are optimized by combining the degree of DRX and the size of recrystallized grain. The optimum hot working window is determined as 1100–1200 °C and 0.1–10 s−1.

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“…By substituting the previous results into Equation (4), the hot deformation equation of the test steel under the deformation at 850–1200 °C and 0.01–10 s −1 can be obtained as follows:

\begin{array}{c}\stackrel{\cdot }{\epsilon }=1.33\times {10}^{15}[\text{sin}h(0.0081\sigma ){]}^{5.96}\text{exp}(-380486/\mathit{\text{R}}T)\end{array}

Section: Resultsmentioning

confidence: 99%

Section: Methodsmentioning

confidence: 99%

Section: Constitutive Equation For Hot Deformationmentioning

confidence: 97%

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Hot Deformation Behavior of a Marine Engineering Steel for Novel 980 MPa Grade Extra‐Thick Plate

Wang,

Ren,

Liu

et al. 2024

steel research int.

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“…Therefore, it is of great significance to study the high-temperature deformation behavior of 301 L stainless steel and to clarify the reasonable hot processing area. [6][7][8][9][10] In addition, due to element segregation during the casting process of 301 L stainless steel, the existence of δ-ferrite at this zone is prone to produce phase boundary cracking in rolling, and a large amount of δ-ferrite can be dissolved after diffusion annealing. [11,12] Now, many researchers have studied the high-temperature properties and microstructure changes of materials.…”

Section: Introductionmentioning

confidence: 99%

Hot Deformation Behavior of 301L Stainless Steel and Dissolution Behavior of δ‐Ferrite During Heat Treatment

Liu

Wang

et al. 2023

steel research int.

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The hot deformation behavior of 301 L stainless steel is investigated at 1000–1250 °C and 0.1–50 s−1. Deformation characteristics are studied through compressive stress–strain curves and constitutive equations. According to the dynamic material model and a series of diffusion annealing experiments, the hot processing map of 301 L stainless steel is established to determine the suitable processing domain. The results show that the stable domain is located in 1085–1240 °C and high strain rate range of 4.5–50 s−1, and the strain rate is the main factor affecting the machinability. Based on the hot compression tests, δ‐ferrite gradually forms a network structure with the increase of temperature; however, it can be inhibited at high strain rate. Therefore, it is necessary to reduce the temperature and increase the strain rate in the actual processing of the machinable area. It is found that diffusion annealing can reduce the content of δ‐ferrite from 12% to 0.67%, and the dissolution of δ‐ferrite is controlled by the diffusion of Cr and Ni, especially noticeable at the interface between γ and δ phase. Finally, the optimum diffusion annealing process parameter is determined at 1300 °C and 10 min.

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“…However, in order to produce process maps for powder metallurgical production processes that start from a porous initial state, important adaptations to the recognized process according to Prasad et al must be made. Because this model only applies to compact materials [19,[24][25][26]. Since the same assumptions as for incompressible materials cannot be made for powder metallurgy components due to their residual porosity and the resulting compressibility, the model must be adapted to compressible materials [27].…”

Section: Introductionmentioning

confidence: 99%

Further Development of Process Maps for TRIP Matrix Composites during Powder Forging

Kirschner¹,

Guk²,

Kawalla³

et al. 2019

MSF

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Process maps according to Parasad et al. are already widely used to make statements about the formability of materials and their forming energy. However, these process maps only apply to conventional incompressible materials. At the TU Bergakademie Freiberg, these process maps have already been extended for particle-reinforced incompressible solid materials with a homogeneous particle distribution. The next step is to adapt the model for compressible particle-reinforced matertials so that they can also be used in powder metallurgy. The problem here is that the volume decreases as a result of compaction during powder forming. In powder metallurgy, however, compaction plays an important role. On the one hand, the compaction of the components leads to an increase in the material properties. On the other hand, pores pose a high risk of fractures and cracking. For this reason, it is the aim of this paper to make the existing process maps for incompressible materials usable for compressible materials by corresponding adaptations of the models prevailing in powder metallurgy. Furthermore, the effects of a homogeneous particle distribution and a graded particle distribution within the TRIP matrix composites on the process maps will be investigated. For this reason, process maps are produced in the temperature ranges between 700 – 1050 °C, with forming speeds of 0.001 – 100 s-1and residual porosity of 10 – 30 %. For this purpose, specimens with corresponding residual porosity and homogeneously distributed ZrO25 vol.%, 10 vol.%, 15 vol.% and 20 vol.% as well as a graded layer structure of corresponding ZrO2proportions are prepared. With the aid of these specimens, flow curves are determined and adjusted at appropriate temperatures and forming speeds during compression tests. The energy dissipation and an instability map are then modelled from these flow curves and a process map is derived. It was found that with increasing ZrO2content in the homogeneous and the graded structure, the areas that allow damage-free forming become smaller. The same applies with decreasing residual porosity. Nevertheless, the areas, which allow failure-free forming, are larger than the possible forming areas of solid components. However, the power dissipation efficiency of incompressible specimens is significantly lower than that of compressible specimen [1]. In addition, it was observed that with increasing ZrO2content and decreasing residual porosity, the efficiency of the power dissipation in the formable areas decreases. It was also found that the distribution of the reinforcing particles has a significant influence on the flow curves and the associated process maps, then the graded specimen do not represent a superposition of the individual process maps of the homogeneous specimens.

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Hot Deformation Behavior and Processing Maps for a Large Marine Crankshaft S34MnV Steel

Cited by 11 publications

References 34 publications

Hot Deformation Behavior of a Marine Engineering Steel for Novel 980 MPa Grade Extra‐Thick Plate

Hot Deformation Behavior of a Marine Engineering Steel for Novel 980 MPa Grade Extra‐Thick Plate

Hot Deformation Behavior of 301L Stainless Steel and Dissolution Behavior of δ‐Ferrite During Heat Treatment

Further Development of Process Maps for TRIP Matrix Composites during Powder Forging

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