Startseite Effect of in situ observation of cooling rates on acicular ferrite nucleation
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Effect of in situ observation of cooling rates on acicular ferrite nucleation

  • Tiantian Wang , Shufeng Yang EMAIL logo , Jingshe Li , Hao Guo und Zhengyang Chen
Veröffentlicht/Copyright: 20. April 2022
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High Temperature Materials and Processes
Aus der Zeitschrift High Temperature Materials and Processes Band 41 Heft 1

Abstract

The effect of cooling rates on acicular ferrite (AF) nucleation was observed in situ by laser scanning confocal microscopy. The precipitation characteristics of TiN–MnS inclusions, the austenite grain size, and the content and morphologies of AF were analyzed and compared under different cooling rates. The results indicated that with the increase of the cooling rate, the size of TiN–MnS inclusions precipitated in the test steel gradually decreased while the inclusion number increased. When the cooling rate increased from 0.2 to 10°C·s−1, the average inclusion size decreased from 2.7 to 1.3 µm. The austenite grain size decreased gradually with the increase of the cooling rate, and the larger the cooling rate was, the more uniform the grain size distribution. The AF proportion increased first and then decreased, it reached the maximum when the cooling rate was 5°C·s−1, which accounted for 82.6%. Meanwhile, the dendrite size decreased gradually, the average length decreased from 30 to 5 µm, and the average width decreased from 2.8 to 0.7 µm when the cooling rate increased from 0.2 to 10°C·s−1.

Keywords: cooling rate; in situ observation; TiN–MnS inclusions; austenite grains; acicular ferrite

1 Introduction

Non-quenched and tempered steel is widely used in major engineering fields such as automobile manufacturing, petrochemical, marine equipment, etc. due to its short manufacturing cycle, energy saving, and excellent mechanical properties [1,2,3]. In recent years, the production and preparation of non-quenched and tempered steel have become the focus of many engineers and researchers as the steel industry pushes toward the production concept of high efficiency, energy saving, and environmental protection [4].

At present, the microstructural uniformity present in non-quenched and tempered steel affects its service life and performance improvement seriously. Many researchers have dealt with this issue mainly in two ways. Among them, some researchers have improved the microstructure and properties of steel by microalloying [5,6,7]. Lu et al. [8,9] found that the morphology of MnS inclusions in non-quenched and tempered steel changed to spherical shape gradually through Zr microalloying, and the inclusion distribution was more uniform. In addition, the polygonal ferrite proportion in the grain was increased, the microstructure was refined effectively, and the plasticity of steel was significantly improved. Mirzaee et al. [10] showed that the addition of the Ti element with mass fractions of 0.7 and 1% made the grain size more uniform, reduced the segregation of Cr and C elements, which significantly improved the microstructure of steel. Javaheri et al. [11] demonstrated that the addition of Nb inhibited the growth of austenite grains and refined the grains sufficiently, which made the size distribution more uniform and properties more outstanding.

Other researchers have improved the microstructure of steel by controlling rolling and the cooling rate [12,13,14]. For example, Bakkaloğlu [15] reduced the rolling temperature from 850 to 740°C and found that the ferrite grain size decreased, the yield strength of the steel increased from 330 to 425 MPa, and the ultimate tensile strength increased from 430 to 528 MPa, the elongation decreased from 38 to 27%. Ghosh et al. [16] found that when the test steel was cooled at the rate of 35°C·s−1, the microstructure of the steel was mainly acicular ferrite (AF), its strength was 888 MPa, and the elongation was 15.3%. When the rate was 1.15°C·s−1, the major microstructure was pearlite, its strength was decreased, and the ductility was greatly improved. However, when the rate cooling was further decreased, the strength did not change significantly. Bu et al. [17] pointed out that increasing the cooling rate inhibited the precipitation of carbides in Ti–Nb–Mo microalloyed steel, and the average microhardness of ferrite grains was gradually reduced. When the cooling rate was 0.5 and 1°C·s−1, a large number of nanoscale carbides NbC and (Ti, Nb, Mo)C precipitated in the test steel, and the ferrite volume fraction was more than 95%. And the microhardness of the ferrite grains exhibited maxima with a cooling rate of 0.5°C·s−1. When the cooling rate increased to 5°C·s−1, only a few carbides of size less than 20 nm precipitated.

Given the above, many researchers tend to improve the microstructure of steel to improve performance. Nevertheless, microstructure transformation often occurs at high temperature, and the traditional metallographic research method cannot observe the high temperature phase transformation and its cooling microstructure transformation directly. Therefore, in this study, laser scanning confocal microscopy (LSCM) was used to observe the dynamic process of phase transformation in situ and study the effect of cooling rates on the precipitation characteristics of AF nucleation site TiN–MnS inclusions and AF nucleation effects, which has an important guiding role in optimizing the controlled cooling process, improving the microstructure and mechanical properties of the steel.

2 Experiments

In this experiment, industrial pure iron, electrolytic manganese, industrial silicon, titanium sponge, and alloys of other elements were used as raw materials. The non-quenched and tempered steel 35 MnVS was melted by a vacuum induction levitation furnace. The chemical composition of the test steel is shown in Table 1.

Table 1

Chemical composition of the test steel (wt%)

C Mn Si S V N Al Ti Mg T[O]
0.36 1.29 0.51 0.054 0.10 0.012 0.041 0.025 0.013 0.0122

Cylindrical samples with a size of Φ7.5 mm × 3 mm were cut from the test steel. All surfaces of samples were ground to keep bright and prevent the sample oxidation surfaces from affecting the experimental process. One of the surfaces was polished and treated as the experimental observation surface. The pretreated sample was placed in acetone and ultrasonically cleaned for 10 min and blow-dried. Then, it was put into an alumina crucible while keeping the polished side up. The crucible was placed under a laser scanning confocal microscope to start the experiment. The cooling intensity of different temperature sections was accurately adjusted by a liquid nitrogen cooling system.

Liquidus temperature of the test steel was 1,480°C calculated by the material property software JMatPro. Based on the results, the heating and cooling process of the test steel was designed. The sample was heated from room temperature to 1,500°C with the rate of 130°C·min−1 first, and then the heating rate was reduced to 10°C·min−1. The heating was stopped when the temperature rose to 1,520°C. The cooling of the test steel was carried out according to the cooling scheme established in Table 2. Argon gas was used as the protective gas throughout the experiment with a gas flow rate of 50 mm3·min−1.

Table 2

Cooling scheme of the test steel in different temperature sections

Cooling section Temperature range Cooling rate (°C·s−1) Other temperature section cooling rate (°C·s−1)
Austenitizing temperature section 1,490°C → 950°C 0.2 1.25
1.25
5
10
Phase transition temperature section 950°C → room temperature 0.2 1.25
1.25
5
10

3 Results and discussion

3.1 TiN–MnS inclusions

There are many factors affecting the formation of AF, such as austenite grain size, cooling rate, steel composition, inclusions, and so on [18,19,20,21]. Research studies have shown that [22] the ability of inclusion-induced AF nucleation depends mainly on its composition and size. TiN–MnS inclusions were one of the main inclusions in the test steel of this study. The distribution of such inclusions was dense and dispersed, which made the induced AF more advantageous in quantity, and thus became the main AF nucleation sites.

Figure 1 shows the precipitation of inclusions observed in situ by LSCM. The composition of these inclusions was detected by energy-dispersive spectrometry (EDS) when the sample was cooled to room temperature. The black spherical inclusions in Figure 1 are primarily composed of Al2O3–MgO. These inclusions have a high melting point and maintain solids at molten steel temperature, their composition and content do not change with the increase or decrease of temperature. When the temperature of the test steel dropped to about 1,410°C, a great number of small-sized TiN–MnS inclusions were precipitated in the steel (arrows in Figure 1). These inclusions were dispersed in the steel and the final precipitated TiN–MnS inclusions made no difference under different cooling rates. Figure 2 shows the EDS results of TiN–MnS inclusions. The average size and number of TiN–MnS inclusions precipitated under different cooling rates were measured and counted by Image-Pro Plus. The results are shown in Figure 3.

Figure 1 The precipitation process of TiN–MnS inclusions.
Figure 1

The precipitation process of TiN–MnS inclusions.

Figure 2 The results of inclusion EDS detection.
Figure 2

The results of inclusion EDS detection.

Figure 3 Comparison of the average size and number of TiN–MnS inclusions under different cooling rates.
Figure 3

Comparison of the average size and number of TiN–MnS inclusions under different cooling rates.

It could be seen from the statistical results that as the cooling rate increased, the average size of the precipitated TiN–MnS inclusions gradually decreased, while the number gradually increased. When the cooling rate was 0.2°C·s−1, the number of inclusions was 249·mm−2 and the average size was 2.7 µm. The number of inclusions was doubled and the average size was reduced by 1.4 µm with the cooling rate increased to 10°C·s−1. As the cooling rate increased, the energy required for inclusion nucleation decreased, and the precipitation was more likely to be promoted. Simultaneously, the time reserved for inclusions from nucleation to growth was shortened, and the inclusions were less likely to collide or grow before they had been precipitated. Therefore, the inclusion size at high cooling rates was relatively small while the inclusion number was large.

Figure 4 shows the process of nucleation and growth of AF on TiN–MnS inclusions observed in situ by LSCM. When the temperature dropped to about 775°C, AF began to nucleate on the inclusions and then continued to grow. When the temperature dropped to 745°C, secondary dendrites appeared on one of the AF dendrites. As the temperature continued to decrease, the number of AF induced by inclusions increased and all of them kept growing in different directions. It could be seen from the figure that AF interlocked with each other. And the AF growth directions were different which was more favorable for forming the self-locking microstructure. Meanwhile, the inclusions were densely and widely distributed and the number of induced AF was also relatively large. The total number of TiN–MnS inclusions in five continuous fields of view and the number of inclusions that could be used as AF nucleation sites were statistically analyzed. The results indicated that approximately 75.0% TiN–MnS inclusions could induce AF well.

Figure 4 AF nucleates on TiN–MnS inclusions.
Figure 4

AF nucleates on TiN–MnS inclusions.

3.2 Austenite grain size

According to the Hall–Petch relationship, the finer the grain is, the higher is the strength [23]. The grain size of the metal material at room temperature is related to the austenite grain size [24,25]. It is well known that the smaller the austenite grain size is, the smaller is the grain size of the transformation product, so it has some influence on the microstructure and properties of the steel. Many scholars [20,26,27,28] believe that the AF content in steel has a great relationship with the austenite grain size. There is a range of austenite grain size, within which the number and size of AF generated reach the optimal balance. When the grain size is outside this range, the proportion of AF decreases. Studies have shown that [28,29] the austenite grain size is not only related to the steel composition, heating rate, holding time, etc. but also related to the cooling rate of molten steel.

Figure 5 shows the morphologies of austenite grains under different rates observed by scanning electron microscopy. AG in the figure represents austenite grain and AGB represents austenite grain boundary. On the whole, the austenite grain size gradually decreased with the increase of the cooling rate. This was due to the high cooling rate of steel, which decreased the time left for the austenite grain boundary migration and the austenite grain growth, making it too late for the grains to grow. The statistical results of austenite grain average size are shown in Figure 6. It could be found that as the cooling rate increased from 0.2 to 1.25, 5, and 10°C·s−1, respectively, the austenite grain average size decreased by 22.2, 53.1, and 70.7%. And the larger the cooling rate was, the more uniformly the austenite grain size was distributed. The difference between the maximum and minimum grain size was only about 30 µm when the cooling rate was 10°C·s−1, while the difference could reach about 100 µm when the cooling rates were 0.2 and 1.25°C·s−1.

Figure 5 Austenite grain morphologies under different cooling rates.
Figure 5

Austenite grain morphologies under different cooling rates.

Figure 6 Austenite grain average size under different cooling rates.
Figure 6

Austenite grain average size under different cooling rates.

3.3 AF morphology

The size of austenite grains is an important factor affecting the nucleation effect of AF. Lee and Pan [30] showed that the critical austenite grain size of AF formed in titanium-killed steel was 50 µm. As the austenite grain size increased, the ability of AF nucleation increased and it began to decrease after reaching a maximum value (180 to 190 µm). Wan et al. [31] observed a critical austenite grain size of AF formed in Zr–Ti compound-deoxidized steel of 55 µm in situ by LSCM. Thewlis [32] carried out a lot of experimental studies, indicating that the intragranular AF content could be maximized when the austenite grain size reached 140 µm. Barbaro et al. [33] believed that more AF could be obtained when the austenite grain size exceeded 110 µm. Therefore, in this study, the critical austenite grain size of forming AF and the maximum AF content were taken as the demarcation point, the austenite grains were divided into small-sized grains, medium-sized grains, and large-sized grains.

Figure 7 shows the AF morphologies in austenite grains of different sizes. SSG in the figure represents small-sized austenite grain, MSG represents medium-sized grain, and LSG represents large-sized austenite grains. Comparing the morphological characteristics of AF under different cooling rates in Figure 7, it was pointed that there was a common phenomenon in the microstructure morphologies under different cooling rates. As the austenite grain size increased from small to large, the number of AF in the grains increased first and then decreased. This is to say, the number and proportion of AF in the medium-sized austenite grains were relatively large, small in small-sized austenite grains relatively, while those of large-sized austenite grains were between them.

Figure 7 AF morphologies in austenite grains of different sizes.
Figure 7

AF morphologies in austenite grains of different sizes.

The statistical results of the AF proportion in austenite grains of different sizes under different cooling rates are shown in Figure 8. The results indicated that with the cooling rate increased, the AF proportion in the austenite grains increased first and then decreased. The proportion was the smallest when the cooling rate was 0.2°C·s−1, and the proportion reached the maximum when the cooling rate was 5°C·s−1. At the four kinds of cooling rates, the AF content in medium-sized austenite grains was the highest and that in the small-sized austenite grains was the lowest. This confirmed that the austenite grain size and the cooling rate affected the AF content of the austenite grains to some extent.

Figure 8 AF proportion in austenite grains of different sizes.
Figure 8

AF proportion in austenite grains of different sizes.

The cooling rate not only affects the AF content in the austenite grains but also affects the morphologies. Figure 9 shows the AF morphologies of the test steel under different cooling rates observed by LSCM. When the cooling rate was 0.2°C·s−1, the AF structure was obliquely crossed and the self-locking property was good but the distribution was relatively scattered. When the cooling rate increased to 1.25°C·s−1 and 5°C·s−1, the AF was crisscrossed with good self-locking properties as the number in the austenite grains was obviously increased and the distribution was uniform and dense. The number and density of AF were decreased and the microstructure distribution was scattered with the cooling rate increased to 10°C·s−1. Simultaneously, it could be seen from the figure that as the cooling rate continued to increase, the size of AF decreased gradually.

Figure 9 AF morphologies under different cooling rates.
Figure 9

AF morphologies under different cooling rates.

The size of AF in the test steel under different cooling rates was measured, and the proportion of AF was counted. The results are shown in Figure 10. The results indicated that the average length and width of AF dendrites in the test steel gradually decreased with the increase of the cooling rate. At a cooling rate of 0.2°C·s−1, the dendrite average length was 30 µm and the average width was 2.8 µm, which was significantly larger than the dendrite size at other cooling rates. When the cooling rate was 10°C·s−1, the dendrite size was the smallest, the average length was only 5 µm, and the average width was 0.7 µm. And the difference of the dendrite average length between these two cooling rates was 25 µm. Figure 10(b) shows the statistical result of the AF proportion under different cooling rates. With the cooling rate increased, the AF proportion increased first and then decreased. When the cooling rate was 0.2°C·s−1, the AF proportion was the smallest, only 13.1%. When the cooling rate increased to 5°C·s−1, the proportion reached the maximum, 82.6%, and the difference between them was about 69.5%. The results were consistent with the statistical results of Figure 8.

Figure 10 Comparison of AF dendrite size and proportion under different cooling rates. (a) AF dendrites size; (b) AF proportion.
Figure 10

Comparison of AF dendrite size and proportion under different cooling rates. (a) AF dendrites size; (b) AF proportion.

The cooling rate has an important influence on the microstructure of the steel. Kang et al. [34] investigated the microstructural evolution of high strength low alloy steel under the continuous cooling rates of 1–50°C·s−1 and found that AF formed at the cooling rate of 10–30°C·s−1. Granular bainite would be formed if the cooling rate was too low while lath-type bainite was dominant when the cooling rate was high. Mun et al. [35] showed that when the cooling rate was 1–5°C·s−1, the microstructure of the test steel was mainly polygonal ferrite. When the cooling rate increased, the ferrite microstructure in the steel became refined and the AF volume fraction increased. The essence of austenite phase transformation is that the carbon atoms in the austenite region are diffused by heating [36]. When the cooling rate is low, the carbon atoms have enough time to diffuse, which will result in the finer ferrite grains previously formed coarse. Then, the adjacent ferritic structure fuses with each other, making the structure coarse again and eventually forming massive granular ferrites. Similarly, granular ferrites will fuse with each other and become larger. Thus, when the cooling rate is low, AF takes a small proportion in the microstructure.

In addition, the decrease of molten steel temperature provides a driving force for austenite phase transformation, which is mainly driven by the degree of undercooling coming from the molten steel [37]. The speed of the cooling rate reflects the degree of undercooling in unit time to some extent. The higher the cooling rate is, the greater is the degree of undercooling of molten steel. The high degree of under cooling will promote the driving force of austenite phase transformation and the precipitation of ferrites. However, when the cooling rate is too high, the degree of under cooling of the molten steel is too large, so the austenite grains are too late to grow and the carbon content inside the grains concentrates, which inhibits the AF nucleation and decrease the AF proportion in the microstructure. Therefore, as the cooling rate increases, the proportion of AF increases first and then decreases.

4 Conclusions

The microstructure uniformity of the steel has a great impact on the improvement of its service life and performance. Therefore, this study improved the microstructure of steel by controlling the cooling rate to improve its performance. Based on the traditional metallographic research method, it is impossible to directly observe the high temperature phase transformation and its cooling microstructure transformation. LSCM was used to observe the dynamic process of phase transformation in situ and study the effect of the cooling rate on the precipitation characteristics of AF nucleation site TiN–MnS inclusions and the AF nucleation effect. Thus, it provided engineering guidance and theoretical basis for optimizing the cooling process and selecting reasonable cooling rates to improve the microstructure and mechanical properties of steel. The following conclusions could be drawn from this study:

  1. In this study, as the cooling rate increased, the size of TiN–MnS inclusions precipitated in the test steel gradually decreased while the number gradually increased. The average size reduced from 2.7 to 1.3 µm while the number increased from 249 to 518 mm−2 with the cooling rate increasing from 0.2 to 10°C·s−1.

  2. When the cooling rate increased from 0.2 to 1.25, 5, and 10°C·s−1, the average austenite grain size in steel decreased by 22.2, 53.1, and 70.7%, respectively. And the larger the cooling rate was, the more uniform the grain size distribution.

  3. As the cooling rate increased, the AF proportion in the test steel increased first and then decreased while the dendrite size gradually decreased. When the cooling rate was 5°C·s−1, the proportion reached the maximum, 82.6%. The dendrite average length decreased from 30 to 5 µm while the average width decreased from 2.8 to 0.7 µm with the cooling rate increasing from 0.2 to 10°C·s−1.

Acknowledgments

The authors gratefully acknowledge the support by the National Natural Science Foundation of China (NSFC, Nos. 51734023 and 51734003).

  1. Funding information: This work was financially supported by the National Natural Science Foundation of China (Great Nos. 51674023 and 51734003).

  2. Author contributions: Tiantian Wang performed the experiments, analyzed the data and wrote the manuscript with help from all the other authors; Shufeng Yang and Jingshe Li helped to perform the analysis with constructive discussions, conceived the work and supervised the whole project; Hao Guo and Zhengyang Chen clarified the logic of the manuscript and revised it.

  3. Conflict of interest: The authors declare no conflict of interest.

  4. Data availability statement: The data used to support the findings of this study cannot be shared at this time as the data also forms part of an ongoing study.

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Received: 2022-02-18
Accepted: 2022-02-18
Published Online: 2022-04-20

© 2022 Tiantian Wang et al., published by De Gruyter

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

Artikel in diesem Heft

  1. Research Articles
  2. Numerical and experimental research on solidification of T2 copper alloy during the twin-roll casting
  3. Discrete probability model-based method for recognition of multicomponent combustible gas explosion hazard sources
  4. Dephosphorization kinetics of high-P-containing reduced iron produced from oolitic hematite ore
  5. In-phase thermomechanical fatigue studies on P92 steel with different hold time
  6. Effect of the weld parameter strategy on mechanical properties of double-sided laser-welded 2195 Al–Li alloy joints with filler wire
  7. The precipitation behavior of second phase in high titanium microalloyed steels and its effect on microstructure and properties of steel
  8. Development of a huge hybrid 3D-printer based on fused deposition modeling (FDM) incorporated with computer numerical control (CNC) machining for industrial applications
  9. Effect of different welding procedures on microstructure and mechanical property of TA15 titanium alloy joint
  10. Single-source-precursor synthesis and characterization of SiAlC(O) ceramics from a hyperbranched polyaluminocarbosilane
  11. Carbothermal reduction of red mud for iron extraction and sodium removal
  12. Reduction swelling mechanism of hematite fluxed briquettes
  13. Effect of in situ observation of cooling rates on acicular ferrite nucleation
  14. Corrosion behavior of WC–Co coating by plasma transferred arc on EH40 steel in low-temperature
  15. Study on the thermodynamic stability and evolution of inclusions in Al–Ti deoxidized steel
  16. Application on oxidation behavior of metallic copper in fire investigation
  17. Microstructural study of concrete performance after exposure to elevated temperatures via considering C–S–H nanostructure changes
  18. Prediction model of interfacial heat transfer coefficient changing with time and ingot diameter
  19. Design, fabrication, and testing of CVI-SiC/SiC turbine blisk under different load spectrums at elevated temperature
  20. Promoting of metallurgical bonding by ultrasonic insert process in steel–aluminum bimetallic castings
  21. Pre-reduction of carbon-containing pellets of high chromium vanadium–titanium magnetite at different temperatures
  22. Optimization of alkali metals discharge performance of blast furnace slag and its extreme value model
  23. Smelting high purity 55SiCr automobile suspension spring steel with different refractories
  24. Investigation into the thermal stability of a novel hot-work die steel 5CrNiMoVNb
  25. Residual stress relaxation considering microstructure evolution in heat treatment of metallic thin-walled part
  26. Experiments of Ti6Al4V manufactured by low-speed wire cut electrical discharge machining and electrical parameters optimization
  27. Effect of chloride ion concentration on stress corrosion cracking and electrochemical corrosion of high manganese steel
  28. Prediction of oxygen-blowing volume in BOF steelmaking process based on BP neural network and incremental learning
  29. Effect of annealing temperature on the structure and properties of FeCoCrNiMo high-entropy alloy
  30. Study on physical properties of Al2O3-based slags used for the self-propagating high-temperature synthesis (SHS) – metallurgy method
  31. Low-temperature corrosion behavior of laser cladding metal-based alloy coatings on EH40 high-strength steel for icebreaker
  32. Study on thermodynamics and dynamics of top slag modification in O5 automobile sheets
  33. Structure optimization of continuous casting tundish with channel-type induction heating using mathematical modeling
  34. Microstructure and mechanical properties of NbC–Ni cermets prepared by microwave sintering
  35. Spider-based FOPID controller design for temperature control in aluminium extrusion process
  36. Prediction model of BOF end-point P and O contents based on PCA–GA–BP neural network
  37. Study on hydrogen-induced stress corrosion of 7N01-T4 aluminum alloy for railway vehicles
  38. Study on the effect of micro-shrinkage porosity on the ultra-low temperature toughness of ferritic ductile iron
  39. Characterization of surface decarburization and oxidation behavior of Cr–Mo cold heading steel
  40. Effect of post-weld heat treatment on the microstructure and mechanical properties of laser-welded joints of SLM-316 L/rolled-316 L
  41. An investigation on as-cast microstructure and homogenization of nickel base superalloy René 65
  42. Effect of multiple laser re-melting on microstructure and properties of Fe-based coating
  43. Experimental study on the preparation of ferrophosphorus alloy using dephosphorization furnace slag by carbothermic reduction
  44. Research on aging behavior and safe storage life prediction of modified double base propellant
  45. Evaluation of the calorific value of exothermic sleeve material by the adiabatic calorimeter
  46. Thermodynamic calculation of phase equilibria in the Al–Fe–Zn–O system
  47. Effect of rare earth Y on microstructure and texture of oriented silicon steel during hot rolling and cold rolling processes
  48. Effect of ambient temperature on the jet characteristics of a swirl oxygen lance with mixed injection of CO2 + O2
  49. Research on the optimisation of the temperature field distribution of a multi microwave source agent system based on group consistency
  50. The dynamic softening identification and constitutive equation establishment of Ti–6.5Al–2Sn–4Zr–4Mo–1W–0.2Si alloy with initial lamellar microstructure
  51. Experimental investigation on microstructural characterization and mechanical properties of plasma arc welded Inconel 617 plates
  52. Numerical simulation and experimental research on cracking mechanism of twin-roll strip casting
  53. A novel method to control stress distribution and machining-induced deformation for thin-walled metallic parts
  54. Review Article
  55. A study on deep reinforcement learning-based crane scheduling model for uncertainty tasks
  56. Topical Issue on Science and Technology of Solar Energy
  57. Synthesis of alkaline-earth Zintl phosphides MZn2P2 (M = Ca, Sr, Ba) from Sn solutions
  58. Dynamics at crystal/melt interface during solidification of multicrystalline silicon
  59. Boron removal from silicon melt by gas blowing technique
  60. Removal of SiC and Si3N4 inclusions in solar cell Si scraps through slag refining
  61. Electrochemical production of silicon
  62. Electrical properties of zinc nitride and zinc tin nitride semiconductor thin films toward photovoltaic applications
  63. Special Issue on The 4th International Conference on Graphene and Novel Nanomaterials (GNN 2022)
  64. Effect of microstructure on tribocorrosion of FH36 low-temperature steels
https://doi.org/10.1515/htmp-2022-0026
Schlagwörter für diesen Artikel
cooling rate; in situ observation; TiN–MnS inclusions; austenite grains; acicular ferrite
Creative Commons
BY 4.0

Artikel in diesem Heft

  1. Research Articles
  2. Numerical and experimental research on solidification of T2 copper alloy during the twin-roll casting
  3. Discrete probability model-based method for recognition of multicomponent combustible gas explosion hazard sources
  4. Dephosphorization kinetics of high-P-containing reduced iron produced from oolitic hematite ore
  5. In-phase thermomechanical fatigue studies on P92 steel with different hold time
  6. Effect of the weld parameter strategy on mechanical properties of double-sided laser-welded 2195 Al–Li alloy joints with filler wire
  7. The precipitation behavior of second phase in high titanium microalloyed steels and its effect on microstructure and properties of steel
  8. Development of a huge hybrid 3D-printer based on fused deposition modeling (FDM) incorporated with computer numerical control (CNC) machining for industrial applications
  9. Effect of different welding procedures on microstructure and mechanical property of TA15 titanium alloy joint
  10. Single-source-precursor synthesis and characterization of SiAlC(O) ceramics from a hyperbranched polyaluminocarbosilane
  11. Carbothermal reduction of red mud for iron extraction and sodium removal
  12. Reduction swelling mechanism of hematite fluxed briquettes
  13. Effect of in situ observation of cooling rates on acicular ferrite nucleation
  14. Corrosion behavior of WC–Co coating by plasma transferred arc on EH40 steel in low-temperature
  15. Study on the thermodynamic stability and evolution of inclusions in Al–Ti deoxidized steel
  16. Application on oxidation behavior of metallic copper in fire investigation
  17. Microstructural study of concrete performance after exposure to elevated temperatures via considering C–S–H nanostructure changes
  18. Prediction model of interfacial heat transfer coefficient changing with time and ingot diameter
  19. Design, fabrication, and testing of CVI-SiC/SiC turbine blisk under different load spectrums at elevated temperature
  20. Promoting of metallurgical bonding by ultrasonic insert process in steel–aluminum bimetallic castings
  21. Pre-reduction of carbon-containing pellets of high chromium vanadium–titanium magnetite at different temperatures
  22. Optimization of alkali metals discharge performance of blast furnace slag and its extreme value model
  23. Smelting high purity 55SiCr automobile suspension spring steel with different refractories
  24. Investigation into the thermal stability of a novel hot-work die steel 5CrNiMoVNb
  25. Residual stress relaxation considering microstructure evolution in heat treatment of metallic thin-walled part
  26. Experiments of Ti6Al4V manufactured by low-speed wire cut electrical discharge machining and electrical parameters optimization
  27. Effect of chloride ion concentration on stress corrosion cracking and electrochemical corrosion of high manganese steel
  28. Prediction of oxygen-blowing volume in BOF steelmaking process based on BP neural network and incremental learning
  29. Effect of annealing temperature on the structure and properties of FeCoCrNiMo high-entropy alloy
  30. Study on physical properties of Al2O3-based slags used for the self-propagating high-temperature synthesis (SHS) – metallurgy method
  31. Low-temperature corrosion behavior of laser cladding metal-based alloy coatings on EH40 high-strength steel for icebreaker
  32. Study on thermodynamics and dynamics of top slag modification in O5 automobile sheets
  33. Structure optimization of continuous casting tundish with channel-type induction heating using mathematical modeling
  34. Microstructure and mechanical properties of NbC–Ni cermets prepared by microwave sintering
  35. Spider-based FOPID controller design for temperature control in aluminium extrusion process
  36. Prediction model of BOF end-point P and O contents based on PCA–GA–BP neural network
  37. Study on hydrogen-induced stress corrosion of 7N01-T4 aluminum alloy for railway vehicles
  38. Study on the effect of micro-shrinkage porosity on the ultra-low temperature toughness of ferritic ductile iron
  39. Characterization of surface decarburization and oxidation behavior of Cr–Mo cold heading steel
  40. Effect of post-weld heat treatment on the microstructure and mechanical properties of laser-welded joints of SLM-316 L/rolled-316 L
  41. An investigation on as-cast microstructure and homogenization of nickel base superalloy René 65
  42. Effect of multiple laser re-melting on microstructure and properties of Fe-based coating
  43. Experimental study on the preparation of ferrophosphorus alloy using dephosphorization furnace slag by carbothermic reduction
  44. Research on aging behavior and safe storage life prediction of modified double base propellant
  45. Evaluation of the calorific value of exothermic sleeve material by the adiabatic calorimeter
  46. Thermodynamic calculation of phase equilibria in the Al–Fe–Zn–O system
  47. Effect of rare earth Y on microstructure and texture of oriented silicon steel during hot rolling and cold rolling processes
  48. Effect of ambient temperature on the jet characteristics of a swirl oxygen lance with mixed injection of CO2 + O2
  49. Research on the optimisation of the temperature field distribution of a multi microwave source agent system based on group consistency
  50. The dynamic softening identification and constitutive equation establishment of Ti–6.5Al–2Sn–4Zr–4Mo–1W–0.2Si alloy with initial lamellar microstructure
  51. Experimental investigation on microstructural characterization and mechanical properties of plasma arc welded Inconel 617 plates
  52. Numerical simulation and experimental research on cracking mechanism of twin-roll strip casting
  53. A novel method to control stress distribution and machining-induced deformation for thin-walled metallic parts
  54. Review Article
  55. A study on deep reinforcement learning-based crane scheduling model for uncertainty tasks
  56. Topical Issue on Science and Technology of Solar Energy
  57. Synthesis of alkaline-earth Zintl phosphides MZn2P2 (M = Ca, Sr, Ba) from Sn solutions
  58. Dynamics at crystal/melt interface during solidification of multicrystalline silicon
  59. Boron removal from silicon melt by gas blowing technique
  60. Removal of SiC and Si3N4 inclusions in solar cell Si scraps through slag refining
  61. Electrochemical production of silicon
  62. Electrical properties of zinc nitride and zinc tin nitride semiconductor thin films toward photovoltaic applications
  63. Special Issue on The 4th International Conference on Graphene and Novel Nanomaterials (GNN 2022)
  64. Effect of microstructure on tribocorrosion of FH36 low-temperature steels
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