Startseite Effect of annealing temperature on the structure and properties of FeCoCrNiMo high-entropy alloy
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Effect of annealing temperature on the structure and properties of FeCoCrNiMo high-entropy alloy

  • Lei Sheng EMAIL logo , Xue Zhengwei , Liu Yafeng , Li Yun , Jiang Dongsheng und Wang Ping
Veröffentlicht/Copyright: 3. August 2022
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High Temperature Materials and Processes
Aus der Zeitschrift High Temperature Materials and Processes Band 41 Heft 1

Abstract

FeCoCrNiMo high-entropy alloy was melted by vacuum arc melting. The alloys were vacuum annealed at 873, 1,073, and 1,273 K, respectively. X-ray diffractometer (XRD), scanning electron microscope (SEM), simultaneous thermal analyzer, microhardness tester, and universal testing machine were used to study the microstructure, the thermal stability, hardness and compression mechanics of as-cast and annealed FeCoCrNiMo alloys. The results show that the alloy is composed of face-centered cubic (FCC) phase and σ phase in both as-cast and annealed states, and the σ phase and μ phase can maintain structural stability at 873 K annealing temperature. The μ phase decomposes to form the σ phase after annealing at 1,073 K, and part of the σ phase dissolves in the FCC phase when annealed at 1,273 K. Both the as-cast and annealed alloys have a typical dendritic structure. The σ phase is enriched in dendrites, and the FCC phase exists between the dendrites. The microstructure of the alloys in the annealed state is more refined than that of the alloy in the as-cast state. In the 1,073 K annealed state, the FeCoCrNiMo alloy has the highest hardness, yield strength, and fracture strength. The fracture mechanism of the alloy is intergranular brittle fracture and cleavage fracture.

Keywords: high-entropy alloys; thermal stability; hardness; compressive properties; microstructure

1 Introduction

In recent years, high-entropy alloys (HEAs) have attracted more and more attention among material and engineering community because they show various exceptional properties, such as extraordinary strength and excellent mechanical properties at high temperature [1].

Usually, some Ni-base superalloys lead to the formation of Fe–Cr-rich TCP phase at 1,173 K, the generation of TCP phase will reduce the solution strengthening effect and decrease the mechanical properties of the alloy. Compared with traditional Ni-base superalloys [2], HEAs have higher stability at high temperature. Thus, they offer potential to replace high temperature materials such as Ni-based superalloys [3,4,5]. As advanced high-temperature structural materials, it is very necessary to study the thermal stability of high-entropy alloy in service [6,7].

Micro alloying of Mo was found to increase the strength of the FeCoCrNi-based HEA alloy, demonstrating the potential of utilizing the solute solution strengthening effect in HEAs. The study on the Mo-alloyed CoCrFeNi HEAs was reported by Shun et al. [8]. The CoCrFeNi alloy exhibits a single face-centered cubic (FCC) solid solution, whereas a (Cr,Mo)-rich σ phase is observed in the face-centered cubic matrix after the addition of Mo into the alloy. The hardness of face-centered cubic matrix and the compressive strength increase with the increase in the Mo concentration.

Nowadays, performance enhancement methods developed for traditional alloys have been successfully applied to HEAs, such as annealing, etc. A CoCrFeNiMo0.3 alloy was 60% rolled and annealed under different conditions, and the σ and μ phases precipitated and strengthened the alloy. The alloy was obtained with a tensile strength of 1.2 GPa, and ductility of 19% [9].

In this work, the FeCoCrNiMo HEAs were prepared by vacuum arc melting. The microstructure evolution at different annealing temperatures was studied. The phase structure and mechanical properties of the alloy were determined. The thermal stability of FeCoCrNiMo alloys were discussed.

2 Experiment

2.1 Material preparation

Fe, Co, Cr, Ni, and Mo (purity >99.9 wt%) were smelted by vacuum arc melting on water-cooled plates in titanium-aspirated Ar gas. The arc-melted ingot was remelted at least five times to ensure the uniformity of composition. After natural cooling, a cylindrical sample with a diameter of 5 mm and a length of 10 mm is cut by wire cutting.

The as-cast and annealed alloys were ground and polished using a grinding machine (Buehler, USA). The microstructures of the samples were exposed after treatment by aqua regia for about 10 s. Then, the samples were subjected to vacuum annealing at 873, 1,073 K, and 1,273 K for 2 h. The surface microstructure of the samples was observed by SEM (Hitachi, Japan). The composition characteristic of as-cast and annealed alloys were analyzed by X-ray diffraction (XRD) (Panalytical, Netherlands). The hardness of the alloy was measured on the mirror surface of the specimen by microhardness tester (Wolpert Wilson, USA), which is set at a load of 0.2 kg with holding time of 15 s. Five measured points were spaced 5 mm apart on the specimen surface, and the average hardness value was calculated. Universal testing machine (Instron, USA) was used to test the compressive properties of the specimens at room temperature and the fracture microstructure was observed. Thermal analysis was performed using a simultaneous thermal analyzer (METTLER TOLEDO, Switzerland) at a heating rate of 20 K·min−1 under a flowing high-purity N2 atmosphere.

3 Results and discussion

3.1 XRD analysis

Figure 1 shows the XRD patterns of FeCoCrNiMo alloy in the as-cast state and at different annealing temperatures. The annealed FeCoCrNiMo alloy is still composed of FCC phase and σ phase, but the μ phase is not detected in the alloy at the annealing temperature of 1,073 K. The diffraction peak intensity of FCC phase in the as-cast state and at different annealing temperatures is the highest, indicating that the FCC phase is the main phase in the as-cast state and the annealing state at different temperatures.

Figure 1 XRD patterns of as-cast and annealed FeCoCrNiMo alloys.
Figure 1

XRD patterns of as-cast and annealed FeCoCrNiMo alloys.

The σ phase has a square structure (lattice parameters a = 9.2443 Å, c = 4.7921 Å, and c/a = 0.5183), and the μ phase has a hexagonal structure (lattice parameters a = 3.5778 Å, c = 25.7538 Å, and c/a = 7.1982). The σ phase effectively increases the strength of the alloy, but reduces the plasticity of the alloy. Due to the increased hardness of the alloy, it is beneficial to improve the wear resistance of the alloy to some extent. The diffraction peak intensity of each phase decreases as the annealing temperature increases [10]. The annealing process enhances diffusion and substitution between elements, resulting in increased unit cell integrity and reduced lattice distortion. At 873 K, the intensity of the σ phase and μ phase diffraction peaks in the alloy is higher, indicating that the Mo-rich σ phase and μ phase can exist stably at 873 K. The μ phase is not detected in the XRD pattern at the annealing temperature of 1,073 K, indicating that the μ phase may be decomposed at 1,073 K.

3.2 Microstructure analysis

Figure 2 shows the microstructure of the FeCoCrNiMo alloy after annealing at different temperatures. The formation of a simple FCC solid solution is due to the fact that the atomic sizes of the four constituent elements, Fe, Co, Cr, and Ni, are approximately the same. There is no significant positive or negative enthalpy of mixing between the elements, as shown in Table 1.

Figure 2 SEMimages of FeCoCrNiMo alloy at different annealing temperatures: (a) As-cast, (b) annealing treatment (AT)-873 K, (c) AT-1,073 K, and (d) AT-1,273 K.
Figure 2

SEMimages of FeCoCrNiMo alloy at different annealing temperatures: (a) As-cast, (b) annealing treatment (AT)-873 K, (c) AT-1,073 K, and (d) AT-1,273 K.

Table 1

Binary mixing enthalpy (unit: kJ·mol−1) and atomic sizes of different elements

Atomic radius (pm) Co Cr Fe Ni Mo
Co (126 pm) — −4 −1 0 −5
Cr (127 pm) −4 — −1 −7 0
Fe (127 pm) −1 −1 — −2 −2
Ni (124 pm) 0 −7 −2 — −7
Mo (190 pm) −5 0 −2 −7 —

The alloy has a typical dendritic structure after casting and heat treatment. The phases of the alloy can be divided into two regions. The main difference between these two regions is the enrichment of Co, Fe, and Ni elements between the dendrites, and the enrichment of Cr and Mo elements in the dendrites. The σ phase and μ phase are mainly distributed within the dendrites. XRD experiment and ref. [11] confirm that the σ phase is rich in Cr and Mo elements. We suggest that the formation of the μ phase is due to the large lattice strain produced by the excess Mo element, which makes the σ phase unable to maintain its tetragonal structure. The release of lattice strain causes the σ phase to transform into the μ phase [11,12].

In Figure 2c and d, it can be seen that a new small block structure is precipitated around the large dendrite. The energy dispersive spectroscopy point analysis and Table 2 reveal that the Mo element content of the dendrites of the as-cast and annealed alloy is higher than that of the interdendrites, and the increase in the Mo content of the main phase may be related to the phase transformation. As the annealing temperature increases, the Mo element content of the dendrites gradually increases from 20.86 to 32.40%, indicating that σ phase is distributed within the dendrites. The release of lattice strain causes the σ phase to transform into the μ phase. Under high temperature annealing treatment, a small amount of μ phase is resolved and re-precipitated into the dendrites. This results in an increased Mo content in the dendrites.

Table 2

Composition distribution of microscopic area in as-cast and annealed FeCoCrNiMo alloys

State Position Nominal chemical composition (at%)
Cr Fe Co Ni Mo
As-cast DR 22.05 19.12 20.84 17.13 20.86
ID 25.52 19.10 20.13 16.14 21.11
AT-873 K DR 22.38 19.76 21.24 16.87 19.75
ID 25.02 18.81 20.62 15.44 20.11
AT-1,073 K DR 22.81 20.16 20.75 17.60 18.68
ID 23.75 17.82 21.88 14.28 22.28
AT-1,273 K DR 22.35 18.38 22.37 14.10 22.80
ID 19.28 17.59 23.19 13.79 26.15

3.3 Thermogravimetric analysis-differential scanning calorimetry (TG-DSC) simultaneous thermal analysis

Figure 3 shows the TG-DSC curve of the FeCoCrNiMo alloy during heating from room temperature to 1,273 K. The TG curve shows that at the beginning of heating up to about 453 K, the alloy powder weight decreases at the highest rate, and then tends to decrease smoothly. The final weight loss is 2.493% during the entire heating process. There are no significant mass changes during the TG test from room temperature to 1,273 K. The result shows that no physical or chemical reactions, such as sublimation and oxidation, occur that alters the quality of the sample [12]. The DSC curve shows a downward trend below 553 K, which is caused by the diffusion of alloying elements into the FCC solid solution at high temperatures to absorb heat. The rise in the DSC curve in the 553–973 K range may be due to the release of lattice distortion energy from the FCC solid solution. And there is no obvious exothermic or endothermic peak in the whole temperature range, indicating that the FeCoCrNiMo alloy has excellent thermal stability [13].

Figure 3 TG-DSC curves of FeCoCrNiMo highentropy alloy.
Figure 3

TG-DSC curves of FeCoCrNiMo highentropy alloy.

3.4 Microhardness analysis

Microhardness of the HEAs was measured on the polished cross-sectional surface using a Vickers hardness tester. A load of 200 g and a holding time of 15 s were applied. With the increase in the annealing temperature, the microhardness increases first and then decreases. It can be seen from Table 3 that when the annealing temperature is 1,073 K, the FeCoCrNiMo alloy has the highest microhardness. The average hardness of the alloy is 699.96HV0.2, which is about 147HV0.2 higher than as-cast. The microhardness of the annealed alloy is higher than that of the as-cast alloy, and the microstructure of the annealed alloy has a wider area of dendrites.

Table 3

Hardness HV0.2 of the FeCoCrNiMo alloy at different annealing temperatures and as-cast

No. As-cast AT-873 K AT-1,073 K AT-1,273 K
1 565.3 670.5 692.0 617.9
2 544.8 663.6 678.9 605.5
3 542.6 623.9 696.2 615.9
4 534.7 681.1 706.3 647.0
5 575.6 645.3 726.4 649.1
Average 552.60 656.88 699.96 627.08

It can be seen from the XRD pattern that the intensity of the diffraction peaks of the σ phase and μ phase in the alloy is higher at 873 K. The σ phase and μ phase play a role in the strengthening and hardening of the alloy, the hardness of the annealed alloy is higher than the hardness of the cast alloy. At annealing temperature of 1,073 K, the excess Mo element decomposes in the μ phase and the interdendritic structures are re-precipitated to form the σ phase, which makes the alloy hardness reach the maximum. A small amount of the σ phase is redissolved at 1,273 K and the hardness of the alloy is reduced [14]. The annealing process provides sufficient energy for the diffusion of the elements, enhancing inter-element diffusion and displacement. Diffusion and displacement between elements is enhanced and the solid solution strengthening effect is reduced.

3.5 Compression performance analysis

Figure 4 shows the compressive stress–strain curves of FeCoCrNiMo alloy in as-cast and annealed state at different annealed temperatures. The compressive yield strength (σ y ), compressive fracture strength (σmax), and compressive deformation rate (ε p) are shown in Table 4. After annealing at 1,073 K, the yield strength and fracture strength of the alloy is 1530.1 and 2180.5 MPa, respectively. After annealing at 1,073 K, the σ phase in the alloy increases. The precipitation strengthening effect is significant, so the yield strength increases [15,16]. With the increase in the annealing temperature, the microstructure of alloy is gradually refined and the strain capacity is enhanced. After annealing at 1,273 K, the highest compressive deformation rate is 14.1%, which is 5.4% higher than that of as-cast alloy.

Table 4

Room temperature compression performance parameters of as-cast and annealed FeCoCrNiMo alloys

State σ y (MPa) σmax (MPa) ε p (%)
As-cast 1308.4 2023.4 8.68
At-873 K 1387.7 2027.3 12.3
At-1,073 K 1530.1 2180.5 12.7
At-1,273 K 1390.9 2030.3 14.1

3.6 Fracture morphology

Figure 5 shows the fracture morphologies of the FeCoCrNiMo alloy. The fracture mechanism is intergranular brittle fracture and cleavage fracture [17]. This result is in accordance with the compression results shown in Figure 4. When cleavage fracture occurs, the crack growth rate in different areas of the cleavage surface is not consistent, which will cause a small amount of tearing cracks [18,19,20,21].

Figure 4 The strain–stress curves of as-cast and annealed FeCoCrNiMo alloys.
Figure 4

The strain–stress curves of as-cast and annealed FeCoCrNiMo alloys.

Figure 5 SEM images of the compression fracture of FeCoCrNiMo alloy: (a) As-cast, (b) AT-873 K, (c) AT-1,073 K, and (d) AT-1,273 K.
Figure 5

SEM images of the compression fracture of FeCoCrNiMo alloy: (a) As-cast, (b) AT-873 K, (c) AT-1,073 K, and (d) AT-1,273 K.

In addition, XRD analysis shows the presence of σ phase in the alloy. The relevant literature [22,23] shows that the presence of the σ phase in the alloy causes a significant reduction in the ductility of the alloy, which can occur even if only a small amount of the σ phase precipitates.

The above results indicate that the FeCoCrNiMo alloy exhibits brittle fracture. This can be attributed to the lattice distortion and the presence of brittle intermetallic compounds [24,25,26], which are inherently very brittle similar to the other types of intermetallic compounds [27,28,29,30]. Due to the poor ductility of brittle intermetallic compounds in FeCoCrNiMo alloy, the alloy shows a strong tendency to form microcavities in crack propagation.

4 Conclusion

  1. The microstructure of the as-cast FeCoCrNiMo alloy was composed of FCC phase, σ phase, and μ phase. The μ phase disappeared after annealing at 1,073 K and the σ phase was formed to re-precipitate in the dendrites.

  2. The hardness at different annealing temperatures was higher than that of as-cast alloys. The analysis results showed that the precipitation of μ phase and σ phase increased the hardness of the alloy. After annealing at 1,073 K, the alloy hardness was 699.96HV0.2 with the highest average hardness. There was no more obvious peak in the DSC curve, indicating excellent thermal stability of FeCoCrNiMo alloy.

  3. FeCoCrNiMo alloy showed the best compressive mechanical properties after annealing at 1,073 K. The compressive strength of this alloy was 2180.5 MPa, and the yield strength is 1530.1 MPa. Fracture analysis showed that the compression fracture mechanism of FeCoCrNiMo alloy in the annealed state was intergranular brittle fracture and cleavage fracture.

Acknowledgments

This work has been supported by the Natural Science Foundation of the Higher Education Institutions of Anhui Province under Grant No. KJ2020ZD42.

  1. Funding information: Natural Science Foundation of the Higher Education Institutions of Anhui Province, China (KJ2020ZD42).

  2. Author contributions: Lei Sheng: resources, writing – original draft, writing – review & editing, methodology, and formal Analysis; Xue Zhengwei: writing – original draft, writing – review & editing, methodology, and formal Analysis; Liu Yafeng: writing – original draft, writing – review & editing, methodology, and formal Analysis; Li Yun: project administration, management and coordination responsibility for the research activity planning and execution; Jiang Dongsheng: project administration, management and coordination responsibility for the research activity planning and execution; Wang Ping: project administration, management and coordination responsibility for the research activity planning and execution.

  3. Conflict of interest: The authors declared that they have no conflicts of interest in this work and do not have any commercial or associative interest that represents a conflict of interest in connection with the work submitted.

  4. Data availability statement: The datasets generated during and/or analyzed during the current study are available from the corresponding author on reasonable request.

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Received: 2022-03-25
Revised: 2022-05-16
Accepted: 2022-06-06
Published Online: 2022-08-03

© 2022 Lei Sheng et al., published by De Gruyter

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

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  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-2022-0048
Schlagwörter für diesen Artikel
high-entropy alloys; thermal stability; hardness; compressive properties; microstructure
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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