Startseite Naturwissenschaften Effects of heat treatment on microstructure and properties of CrVNiAlCu high-entropy alloy
Artikel Open Access

Effects of heat treatment on microstructure and properties of CrVNiAlCu high-entropy alloy

  • Shijie Bai , Yifeng Xiao EMAIL logo , Liang Wu und Qiankun Zhang
Veröffentlicht/Copyright: 18. Februar 2025
Artikel downloaden (PDF)
High Temperature Materials and Processes
Aus der Zeitschrift High Temperature Materials and Processes Band 44 Heft 1

Abstract

This study employs X-ray diffraction, scanning electron microscopy, electrochemical workstations, and hardness testers to evaluate the impact of annealing temperatures (600, 700, and 800°C) on the microstructure and corrosion resistance of the CrVNiAlCu high-entropy alloy. Findings demonstrate that the as-cast alloy is composed of copper-rich FCC and chromium-rich BCC phases. With increasing annealing temperatures, the alloy’s crystals transform into dendritic structures, accompanied by the precipitation of new phases. The as-cast alloy displays a peak hardness of 674 HV, which significantly reduces after annealing. Moreover, annealing treatment reduces lattice distortion and element segregation in the alloy, thereby improving the corrosion resistance of the alloy. Importantly, the alloy attains its highest corrosion resistance after annealing at 800°C.

Keywords: high-entropy alloy; heat treatment; microstructure; corrosion resistance

1 Introduction

High-entropy alloys (HEAs) are defined as solid solution alloys comprising five or more principal elements, with atomic concentrations ranging from 5 to 35% [1,2,3,4]. The high entropy of mixing reduces the Gibbs free energy, facilitating the formation of simple crystalline structures, thereby preventing the development of complex intermetallic compounds or brittle phases. Consequently, HEA usually consist of single-phase FCC, single-phase BCC, or mixed FCC and BCC structures [5,6]. They exhibit excellent corrosion resistance, high strength, toughness, and resistance to high-temperature oxidation [7,8]. Domestic and international scholars have conducted extensive research on the corrosion behavior of numerous HEA in various heat treatment conditions and corrosive environments.

Yang et al. [9] investigated the impact of Al content on the microstructure of AlxCoCrFeNi HEA. Their results indicated that the alloy’s phase structure transitioned from a single FCC phase to an FCC and ordered B2 phase, eventually evolving into an A2 + B2 phase as Al content increased, suggesting that higher Al content promotes the formation of a B2 phase between Ni and Al. Zhang et al. [10] investigated the corrosion resistance of AlCoCrFeNiCu alloys in different states in a 3.5% NaCl solution, revealing that annealed alloys exhibited increased dendritic regions compared to as-cast alloys, and corrosion transitioned from intergranular and pitting to single-point corrosion. An appropriate annealing temperature significantly influences the corrosion resistance of HEA. Lin et al. [11] found that Cu0.5CoCrFeNi HEA subjected to aging heat treatment between 350 and 950°C exhibited severe corrosion, with copper-rich precipitates forming in the FCC matrix, leading to a notable potential difference. However, heat treatment between 1,100 and 1,350°C improved corrosion resistance by dissolving copper-rich phases into the FCC matrix. Additional research [12,13,14,15,16] demonstrates that HEA’ microstructure inhomogeneity increases their corrosion tendency, primarily due to copper-rich or aluminum-rich phases precipitating in the matrix with a substantial potential difference. These findings underscore the significant influence of alloy composition and heat treatment state on HEA’ microstructure and corrosion resistance.

The present study synthesized a CrVNiAlCu HEA using a vacuum, non-self-consuming arc melting process, investigating how heat treatment affects its crystal structure, microstructure, mechanical properties, and corrosion resistance. The findings provide experimental data to advance the development of HEA.

2 Experimental method

CrVNiAlCu HEA was synthesized by vacuum arc melting in a copper mold under argon. Commercial-grade elements (Cr, V, Ni, Al, and Cu) with 99.5% purity were used as the raw materials. The ingot was then cut into 5 mm × 5 mm × 5 mm block samples for analysis of the crystal structure, microstructure, and corrosion resistance. Each batch of four samples was annealed at 600, 700, and 800°C for 2 h before cooling in the furnace, with a heating rate of 10°C·min−1. The samples were ground and polished to achieve a flat surface. Next the samples were etched using aqua regia for scanning electron microscopy (SEM, model EVO MA10) analysis. The microstructure was investigated by SEM, and the composition was determined by energy-dispersive spectrometry (EDS, model OXFORD INCA). The crystal structure was examined by X-ray diffraction (XRD; Rigaku D/Max 2500/X) using Cu Kα radiation at a scanning rate of 8°/min and a 2θ range of 10–90°. The hardness was measured under a load of 0.2 kg for a duration of 10 s by using a Vickers hardness tester (TMHV-1000). Twelve different locations were measured to calculate the average hardness and standard deviation. A CS350 electrochemical workstation was used to conduct the electrochemical experiments, with the electrolyte consisting of a uniform 3.5 wt% NaCl solution. The samples served as the working electrode, platinum sheet served as the auxiliary electrode, and a saturated calomel electrode served as the reference electrode in a three-electrode system. Electrochemical impedance spectroscopy was carried out from 100 kHz to 0.01 Hz with an amplitude of 10 mV after waiting for the open circuit potential to stabilize. The dynamic potential polarization experiment used a 1 mV·s−1 scan rate with a −1.5 V (vs E ocp) to 1.5 V (vs E ocp) scan potential range.

3 Results and discussion

3.1 Microstructure

XRD diffraction spectra for CrVNiAlCu HEA in the as-cast and three distinct annealed states are displayed in Figure 1. According to a comparison with the standard PDF card database, the as-cast CrVNiAlCu HEA exhibits a two-phase structure. The diffraction peaks at 2θ = 44.370°, 64.552°, and 81.690° represent the structure of the BCC solid solution. These diffraction peaks are consistent with the PDF card of Cr (JCPDS No. 851336), but the corresponding diffraction angle is shifted to the left, which represent a Cr-rich phase with lattice distortion. The diffraction peaks at 2θ = 43.190°, 50.299°, 73.885°, and 81.690° represent the structure of the FCC solid solution. These diffraction peaks are consistent with the PDF card of Cu (JCPDS No. 70-3038), but the corresponding diffraction angle is shifted, which represent a Cu-rich phase with lattice distortion. Following annealing at 600°C, the new diffraction peaks exhibited positions at 2θ = 31° and 55°. These diffraction peaks are consistent with the PDF card of Al-Ni (JCPDS No. 65-0420), indicating an ordered B2 phase. Following annealing at 700°C, new diffraction peaks emerged at approximately 2θ = 43°, 63°, and 79°. These diffraction peaks are consistent with the PDF card of (JCPDS No. 65-6819) of the V-Cr phase with a body-centered cubic structure. It can also be observed that the intensity of the corresponding peak for the (110) crystal plane of the Cr-rich phase in the alloy decreases. This indicates that V atoms with larger atomic radii diffuse into the Cr lattice, partially transforming into the V-Cr phase and partially causing lattice expansion in the Cr-rich phase. Following annealing at 800°C, a new diffraction peak was observed in the diffraction pattern at approximately 2θ = 26°. Its diffraction pattern is consistent with the PDF card (JCPDS No. 52-0922) of AlCrCu2 with an FCC structure. As the annealing temperature increases, phase precipitation becomes more pronounced. This occurs because the rapid cooling of the cast alloy through a water-cooled copper disc leads to severe crystal distortion and delayed diffusion. The annealing treatment provides the energy required for atomic diffusion within the cast alloy, enabling the precipitation of new phases from the supersaturated solid solution.

Figure 1 XRD diffraction spectra of CrVNiAlCu HEA in cast and annealed states.
Figure 1

XRD diffraction spectra of CrVNiAlCu HEA in cast and annealed states.

Figure 2 displays the SEM microstructure of the CrVNiAlCu alloy in the as-cast state and after annealing at three different temperatures. Table 1 presents the EDS elemental analysis results for each point depicted in Figure 2. In the as-cast alloy, the black phase is distributed in a snowflake-like morphology within the dark gray phase, and the white phase is situated within the intergranular regions of the gray phase. Combined XRD and EDS analyses indicate that the black and dark gray phases comprise V-Cr-rich BCC structures, whereas the white and gray phases comprise Ni-Cu-rich FCC structures. This segregation phenomenon is attributed to the mixing enthalpy among the elements [17], as illustrated in Table 2. The lower enthalpy of binary mixing between V and Al, Ni, and Cr indicates a weak bonding capacity among atoms, which hinders the ordered rearrangement of atoms. Consequently, as the temperature rises, part of Al and Ni tend to aggregate in the V-Cr solid solution, forming an unstable, supersaturated black BCC solid solution phase. The mixing enthalpy of Cu with the binary mixture of V, Cr, and Ni is high, resulting in weaker interatomic forces. Additionally, the melting temperature of copper is lower than that of V, Cr, and Ni. Therefore, it is relatively straightforward for Cu to precipitate in the intergranular spaces, forming a white FCC solid solution phase at lower temperatures. As shown in Figure 2(b), following annealing at 600°C, the large snowflake-like black phases vanish from the alloy, while the white phase area expands, with some black phases emerging within it. This phenomenon is attributed to the diffusion of Al and Ni atoms, which possess strong atomic bonding energy, from the black phase region and their aggregation within the white interdendritic FCC phase, resulting in the formation of an ordered B2 phase. In Figure 2(c), following annealing at 700°C, the area occupied by the black phase of the alloy is significantly reduced and disperses into the gray phase. This occurs due to a portion of the supersaturated disordered BCC solid solution transforming into the ordered V-Cr and B2 phase, while the rest transforms into a dark grey ordered BCC phase. As a result, the dark gray phase continues to grow into a microstructure of the lath, but its volume fraction decreases. In Figure 2(d), in contrast to the alloy annealed at 700°C, the grain size of the black phase is significantly smaller and uniformly dispersed within the gray phase. Furthermore, the ordered BCC dark gray phase develops into dendritic crystals. As the dark gray phase grows and coarsens, elements in the Cu-rich white phase migrate toward the light gray phase, leading to the growth of ordered FCC structures.

Figure 2 Backscattered electron SEM microstructures of CrVNiAlCu HEA: (a) As-cast, (b) 600°C, (c) 700°C, and (d) 800°C.
Figure 2

Backscattered electron SEM microstructures of CrVNiAlCu HEA: (a) As-cast, (b) 600°C, (c) 700°C, and (d) 800°C.

Table 1

EDS composition results of CrVNiAlCu HEA (at%)

Alloy condition Point Al V Cr Ni Cu
As-cast a1 11.56 36.15 22.95 18.07 11.27
b1 5.31 19.68 58.49 12.70 3.82
c1 19.51 5.02 10.48 43.01 21.99
d1 12.22 1.17 4.69 13.52 68.39
600°C a2 10.64 35.41 23.34 19.82 10.79
b2 8.19 20.62 57.44 10.78 2.97
c2 30.20 5.15 9.81 37.93 16.91
d2 16.82 0.99 2.76 13.33 66.11
700°C a3 35.83 12.58 10.11 27.06 14.43
b3 7.64 39.07 41.17 9.66 2.47
c3 31.75 8.94 6.08 35.66 17.57
d3 19.38 1.37 1.40 10.37 67.48
800°C a4 36.52 12.41 9.42 28.64 13.01
b4 7.88 37.37 41.33 11.07 2.35
c4 33.23 7.40 3.89 36.57 18.92
d4 20.74 1.17 1.42 11.97 64.69
Table 2

Values of Δ H i j mix for binary liquid metals

Δ H mix (kJ·mol−1) Al V Cr Ni Cu
Al 0 −16 −10 −22 −1
V 0 −2 −18 5
Cr 0 −7 12
Ni 0 4
Cu 0

3.2 Microhardness

On the alloy surface, 12 positions were selected every 0.5 mm spacing for microhardness tests. Figure 3 shows the average Vickers hardness value of the CrVNiAlCu HEA. The hardness value of the alloy surface first decreases, then increases, and then decreases with increasing annealing temperature. The combination of XRD and SEM results indicates that the high hardness of the cast alloys is attributed to the presence of oversaturated disordered BCC and FCC phases, which cause significant lattice distortions. Therefore, the cast alloy exhibits the highest hardness value of 674 HV. In the alloy annealed at 600°C, the outward diffusion of disordered BCC black phase atoms and the decrease in the volume fraction of the black phase lead to a decrease in the alloy’s resistance to deformation, thereby reducing the alloy’s micro-Vickers hardness. After annealing at 700°C, the Cr-rich black disordered BCC phase disappears, and a spherical tough B2 phase with higher hardness precipitates. The diffusion of Cr and V atoms from the black phase into the dark grey phase to form the V-Cr phase causes a large number of lattice distortions. This resulted in an increase in the alloy’s hardness to 552 HV. In the alloy annealed at 800°C, although the grain size of the dark gray BCC phase increases and a new FCC phase is formed, the strengthening effect of BCC relative to the alloy cannot compensate for the weakening of the relative hardness of FCC. Consequently, the hardness of the alloy annealed at 800°C decreased to 511 HV.

Figure 3 Micro Vickers hardness of CrVNiAlCu HEA.
Figure 3

Micro Vickers hardness of CrVNiAlCu HEA.

3.3 Corrosion resistance

Figure 4 shows the results of dynamic potential polarization experiment of CrVNiAlCu HEA in 3.5 wt% NaCl solution. The anode part of the alloy dynamic potential scanning curve has a section where the current density growth slows down. Although there is no obvious passivation transition zone in the curve, this trend in current density indicates that the alloy has passivation effect. This suggests the formation of a protective Al2O3 or Cr2O3 layer by aluminum and chromium in the alloy. Further, compared with directly cast alloys, the Tafel zone of the alloys annealed at 600 and 800°C shifted to the lower left direction, indicating an improved corrosion resistance of the annealed alloys. This enhancement may be due to the fact that at these annealing temperatures the lattice distortion energy of the alloy is smaller and the potential difference between the phases is smaller, making it easier to form a more stable and protective oxide film.

Figure 4 The potentiodynamic polarization curves of CrVNiAlCu HEA in 3.5 wt% NaCl corrosion solution.
Figure 4

The potentiodynamic polarization curves of CrVNiAlCu HEA in 3.5 wt% NaCl corrosion solution.

The Tafel zone of the polarization curves of CrVNiAlCu HEA in cast and annealed condition in 3.5 wt% NaCl solution was fitted to obtain the corrosion parameters in Table 3. As-cast HEAs have the highest corrosion current density, indicating that their corrosion resistance is the poorest. The FCC phase between dendrites of the as-cast HEA is rich in Cu and Ni elements, and its standard electrode potential is high (Cu +0.33 V, Ni −0.25 V). Its priority for generating a passivation film is lower than that of the BCC phase (V −1.175 V, Cr −0.913 V). Due to the potential difference between the two phases, the FCC phase preferentially corrodes. The HEA annealed at 800°C exhibits the lowest corrosion current density, indicating superior corrosion resistance [10]. Although its corrosion potential E corr and breakdown potential E pit are slightly higher than those of other states, the passivation zone is wider. This means that the corrosion tendency of CrVNiAlCu HEA annealed at 800°C is higher, but its resistance to pitting corrosion is strong. At 600°C, annealing significantly lowers the current density compared to the cast alloy. This improvement is attributed to better structural organization, reduced lattice distortion in the black BCC phase, fewer defects, and overall enhanced corrosion resistance. However, increasing the annealing temperature to 700°C results in higher corrosion voltage and current density, alongside a reduced passivation region (ΔE), indicating a lesser tendency for corrosion but decreased resistance to both general and pitting corrosion. This is attributed to the growth of the dark gray BCC phase, which causes severe lattice distortions. Additionally, the segregation of Cu at grain boundaries during the diffusion process of atoms allows Cl− ions to preferentially attack the Cu-rich, weakening the alloy’s corrosion defense [11]. When the annealing temperature reaches 800°C, the growth of the B2 phase is suppressed, the distribution of BCC phases rich in V-Cr is more uniform and widespread, and the Cu elements at the grain boundaries integrate into the matrix. Consequently, the alloy at this annealing temperature has the highest corrosion resistance.

Table 3

Corrosion parameters of CrVNiAlCu HEA in 3.5 wt% NaCl solution

Condition E corr (V) I corr (A·cm−2) E pit (V) ∆E (V)
As-cast −0.51 7.31 × 10−6 −0.11 0.40
Annealed at 600°C −0.62 1.61 × 10−6 −0.15 0.47
Annealed at 700°C −0.39 2.31 × 10−6 −0.14 0.25
Annealed at 800°C −0.68 1.43 × 10−6 −0.19 0.50

The Nyquist, Bode, and equivalent circuit diagrams of CrVNiAlCu HEA in 3.5 wt% NaCl solution are shown in Figure 5. In an equivalent circuit, R s is equivalent to the total impedance value in series in the solution, R ct is equivalent to the resistance of charge transfer on the working surface of the electrode, and R f is the impedance value of the passivation film on the working electrode. The uneven and rough surface of the alloy sample results in an unstable response ability of the double-layer capacitance at the electrode interface to interference frequency. Consequently, substituting capacitor with a constant phase angle component can enhance the precision of the equivalent circuit impedance. CPEdl represents the capacitance of the double layer on the surface of the sample, while CPEdiff denotes the capacitance that generates a passivation film on the working electrode. The Nyquist curve of the as-cast HEA exhibits a single capacitive arc, with its center of circle located in the fourth quadrant of the coordinate axis. This indicates that charge transfer occurs on an uneven electrode surface [17]. The Bode plot of cast CrVNiAlCu HEA has only one single peak, indicating that it is controlled by only one time constant. In light of the severe element segregation and uneven working surface of the CrVNiAlCu HEA as cast, it can be postulated that this time constant may be controlled by the coincidence of two time constants [18,19,20,21]. Consequently, an equivalent circuit comprising two capacitors is used to fit the Nyquist plot of the as-cast HEA. The larger the radius of the capacitor arc in the Nyquist diagram, the stronger the corrosion resistance of the material. In addition, the phase angle in the Bode plot indicates the corrosion resistance of the material. The higher the phase angle, the greater the corrosion resistance. The corrosion resistance of cast CrVNiAlCu HEA is the worst, while HEA achieved the best corrosion resistance at an annealing temperature of 800°C.

Figure 5 (a) Nyquist diagram; and (b) Bode and phase angle diagram of CrVNiAlCu HEA in 3.5 wt% NaCl corrosion solution.
Figure 5

(a) Nyquist diagram; and (b) Bode and phase angle diagram of CrVNiAlCu HEA in 3.5 wt% NaCl corrosion solution.

Table 4 shows the results of impedance fitting for four types of HEAs using equivalent circuits. The larger the R ct, the fewer ions and electrons pass through the double layer capacitance and the alloy has better corrosion resistance [18]. Consequently, the minimal passage of ions and electrons occurs in the alloy annealed at 800°C. R f has the same rule as R ct. The R f of the alloy significantly exceeds R ct, indicating that the corrosion resistance of the CrVNiAlCu alloy is predominantly governed by the formation of a passivation film. Within the passivation film corrosion system, the size of impedance arc radius correlates with the passivation film’s stability, thickness, and integrity [22], whereas CPEdiff inversely relates to the film’s thickness [23]. Annealing at 800°C results in the thickest passivation film, offering the highest corrosion resistance; notably, the alloy’s corrosion resistance post-annealing at 600°C surpasses that observed at 700°C.

Table 4

Impedance fitting parameters of CrVNiAlCu HEA in 3.5 wt% NaCl corrosion solution

Condition R s (Ω·cm−2) R ct (Ω·cm−2) CPEdl (S·secn·cm−2) n1 R f (Ω·cm−2) CPEdiff (S·secn·cm−2) n2
As-cast 1.31 23.19 1.41 × 10−5 0.55 8.67 × 103 2.72 × 10−4 0.98
600°C 0.92 30.27 2.28 × 10−5 0.51 6.93 × 104 2.83 × 10−5 0.61
700°C 1.48 25.12 2.69 × 10−5 0.87 4.08 × 104 4.14 × 10−5 0.85
800°C 1.21 55.22 2.91 × 10−5 0.83 2.90 × 105 1.47 × 10−5 0.67

Based on the previous organizational analysis, it can be concluded that corrosion resistance is related to the number of defects and component segregation within HEA. The lattice defect and compositional segregation are most severe in the as-cast alloy, with the greatest potential difference observed between the BCC phase rich in V-Cr and the FCC phase rich in Cu-Ni. Consequently, as-cast HEA exhibit the lowest corrosion resistance. Following annealing at 600°C, the Al and Ni elements present in the original black phase diffuse into the grey phase, thereby forming a new black phase. This process reduces the lattice distortion and the number of defects. Consequently, the corrosion resistance of the alloy is enhanced. As the annealing temperature increases to 700°C, the volume fraction of the corrosion-resistant dark gray phase decreases, and the V-Cr phase precipitates from it. The expansion of the B2 phase within the gray-white FCC phase increases the contact area between different phase regions. The increase in these defects serves to exacerbate the corrosion potential difference between different phases within the alloy, thereby reducing its corrosion resistance. At 800°C, the growth of the black B2 phase in the alloy is inhibited, while the volume fraction of the Cr-rich BCC phase increases, thus enhancing the corrosion resistance of the CrVNiAlCu HEA. This conclusion is corroborated by the electrochemical test fit analysis.

4 Conclusion

This study examines the effects of annealing heat treatment at various temperatures on the microstructure and corrosion resistance of CrVNiAlCu HEA. The as-cast CrVNiAlCu HEA consists of a Cr-V-rich BCC phase and a Cu-Ni-rich FCC phase. The as-cast alloy has a Vickers hardness value of 674 HV and the poorest corrosion resistance. At an annealing temperature of 600°C, the area of the black BCC phase decreased, leading to the precipitation of an ordered B2 phase. The area of the Cr-V-rich dark grey phase expanded, significantly reducing the lattice distortions in the alloy. Consequently, the hardness of the alloy decreased from 674 to 534 HV, and its corrosion resistance substantially improved. At an annealing temperature of 700°C, the V-Cr-rich black BCC phase dissipated, leading to the formation of a new, dispersed Ni-Al-rich black phase within the grey phase. With the decreased volume fraction of dark grey BCC phase, precipitating V-Cr intermetallic compounds, the alloy underwent severe lattice distortions. This change increased the alloy’s hardness to 552 HV and a slight reduction in its corrosion resistance. At an annealing temperature of 800°C, the enhancement of atomic diffusion ability reduces the compositional segregation in the alloy. The crystals of the dark grey phase grew into large dendrites, while the growth of the Ni-Al-rich black phase was inhibited. As a result, the hardness of the alloy decreased to 511 HV, yet it exhibited the best corrosion resistance.

Acknowledgements

The authors sincerely acknowledge the support of the School of Mechanical Engineering and Mechanics at Xiangtan University for providing experimental equipment and materials for this study.

  1. Funding information: Authors state no funding involved.

  2. Author contributions: Shijie Bai, Qiankun Zhang, Liang Wu, and Yifeng Xiao conceived and designed the experiments; Shijie Bai, Qiankun Zhang, and Yifeng Xiao performed the experiments; Shijie Bai, Liang Wu, and Yifeng Xiao analyzed the data; Shijie Bai wrote the original draft; Yifeng Xiao provided the guidance for writing.

  3. Conflict of interest: Authors state no conflict of interest.

  4. Data availability statement: The data used to support the findings of this study are included within the article.

References

[1] Yeh, J. W., S. K. Chen, S. J. Lin, J. Y. Gan, T. S. Chin, T. T. Shun, et al. Nanostructured high-entropy alloys with multiple principal elements: novel alloy design concepts and outcomes. Advanced Engineering Materials, Vol. 6, No. 5, 2004, pp. 299–303.10.1002/adem.200300567Suche in Google Scholar

[2] Bridges, D., D. Fieser, J. J. Santiago, and H. Anming. Novel frontiers in high-entropy alloys. Metals, Vol. 13, No. 7, 2023, id. 1193.10.3390/met13071193Suche in Google Scholar

[3] George, E. P., D. Raabe, and R. O. Ritchie. High-entropy alloys. Nature Reviews Materials, Vol. 4, No. 8, 2019, pp. 515–534.10.1038/s41578-019-0121-4Suche in Google Scholar

[4] Murty, B. S., J. W. Yeh, S. Ranganathan, and P. P. Bhattacharjee. High-entropy alloys, Elsevier, Amsterdam, 2019.10.1016/B978-0-12-816067-1.00009-6Suche in Google Scholar

[5] Ran, R., Y. Zhang, Y. Wang, and G. Wang. Effect of annealing treatment on precipitates and tensile properties of FeCoCrNiVN high-entropy alloy produced by twin-roll casting. Journal of Materials Engineering and Performance, Vol. 33, No. 1, 2024, pp. 3374–3383.10.1007/s11665-023-08239-zSuche in Google Scholar

[6] Yazdani, N., M. Toroghinejad, A. Shabani, and P. Cavaliere. Effects of process control agent amount, milling time, and annealing heat treatment on the microstructure of AlCrCuFeNi high-entropy alloy synthesized through mechanical alloying. Metals, Vol. 11, No. 9, 2021, id. 1493.10.3390/met11091493Suche in Google Scholar

[7] Xiao, Y., Y. Zou, H. Ma, A. S. Sologubenko, X. Maeder, R. Spolenak, et al. Nanostructured NbMoTaW high entropy alloy thin films: High strength and enhanced fracture toughness. Scripta Materialia, Vol. 168, 2019, pp. 51–55.10.1016/j.scriptamat.2019.04.011Suche in Google Scholar

[8] Nene, S. S., M. Frank, K. Liu, S. Sinha, R. S. Mishra, B. A. McWilliams, et al. Corrosion-resistant high entropy alloy with high strength and ductility. Scripta Materialia, Vol. 166, 2019, pp. 168–172.10.1016/j.scriptamat.2019.03.028Suche in Google Scholar

[9] Yang, T., S. Xia, S. Liu, C. Wang, S. Liu, Y. Zhang, et al. Effects of Al addition on microstructure and mechanical properties of AlxCoCrFeNi high-entropy alloy. Materials Science and Engineering: A, Vol. 648, 2015, pp. 15–22.10.1016/j.msea.2015.09.034Suche in Google Scholar

[10] Zhang, X., J. Guo, X. Zhang, Y. Song, Z. Li, X. Xing, et al. Influence of remelting and annealing treatment on corrosion resistance of AlFeNiCoCuCr high entropy alloy in 3.5% NaCl solution. Journal of Alloys and Compounds, Vol. 775, 2019, pp. 565–570.10.1016/j.jallcom.2018.10.081Suche in Google Scholar

[11] Lin, C., H. Tsai, and H. Bor. Effect of aging treatment on microstructure and properties of high-entropy Cu0.5CoCrFeNi alloy. Intermetallics, Vol. 18, No. 6, 2010, pp. 1244–1250.10.1016/j.intermet.2010.03.030Suche in Google Scholar

[12] Nong, Z., Z. Zhang, H. Wang, and X. Deng. Microstructure inhomogeneity of as-cast high-entropy alloy and heat treatment improvement. Materials Science and Technology, Vol. 35, No. 14, 2019, pp. 1749–1755.10.1080/02670836.2019.1647383Suche in Google Scholar

[13] Zhang, H., J. Cai, J. Geng, X. Sun, Y. Zhao, X. Guo, et al. Study on annealing treatment of NbMoTaTiNi high-entropy alloy with ultra-high strength disordered-ordered transition structure for additive manufacturing. Journal of Alloys and Compounds, Vol. 943, 2023, id. 168810.10.1016/j.jallcom.2023.168810Suche in Google Scholar

[14] Lin, C. and H. Tsai. Effect of annealing treatment on microstructure and properties of high-entropy FeCoNiCrCu0.5 alloy. Materials Chemistry and Physics, Vol. 128, No. 1, 2011, pp. 50–56.10.1016/j.matchemphys.2011.02.022Suche in Google Scholar

[15] Zhao, J. H., X. L. Ji, Y. P. Shan, Y. Fu, and Z. Yao. On the microstructure and erosion–corrosion resistance of AlCrFeCoNiCu high-entropy alloy via annealing treatment. Materials Science and Technology, Vol. 32, No. 12, 2016, pp. 1271–1275.10.1080/02670836.2015.1116494Suche in Google Scholar

[16] Peng, Y., G. Zhou, J. Han, J. Li, H. Zhang, S. Zhang, et al. Effect of heat treatment on the corrosion resistance of AlFeCoNiMo0.2 high-entropy alloy in NaCl and H2SO4 solutions. Metals, Vol. 13, No. 5, 2023, id. 849.10.3390/met13050849Suche in Google Scholar

[17] Ponomareva, A. V., M. P. Belov, E. A. Smirnova, K. V. Karavaev, K. Sidnov, B. O. Mukhamedov, et al. Theoretical description of thermodynamic and mechanical properties of multicomponent BCC Fe-Cr-based alloys. Physical Review Materials, Vol. 4, No. 9, 2020, id. 094406.10.1103/PhysRevMaterials.4.094406Suche in Google Scholar

[18] Muñoz, A. I., J. G. Antón, J. L. Guiñón, and V. P. Herranz. Inhibition effect of chromate on the passivation and pitting corrosion of a duplex stainless steel in LiBr solutions using electrochemical techniques. Corrosion Science, Vol. 49, No. 8, 2007, pp. 3200–3225.10.1016/j.corsci.2007.03.002Suche in Google Scholar

[19] Yunzhu, S. In-situ electrochemical-AFM study of localized corrosion of AlxCoCrFeNi high-entropy alloys in chloride solution. Applied Surface Science, Vol. 439, 2018, pp. 533–544.10.1016/j.apsusc.2018.01.047Suche in Google Scholar

[20] Qiu, Y., S. Thomas, M. A. Gibson, H. L. Fraser, and N. Birbilis. Corrosion of high-entropy alloys. npj Materials Degradation, Vol. 1, No. 1, 2017, id. 15.10.1038/s41529-017-0009-ySuche in Google Scholar

[21] Hsu, K. M., W. L. Chien, and C. S. Lin. The improved stability and corrosion resistance of the passive film on Mn-containing FeCrNiCoMnx high-entropy alloys by multiple pickling. Journal of Alloys and Compounds, Vol. 962, 2023, id. 171141.10.1016/j.jallcom.2023.171141Suche in Google Scholar

[22] Carnot, A., I. Frateur, S. Zanna, B. Tribollet, I. D. Brugger, and P. Marcus. Corrosion mechanisms of steel concrete moulds in contact with a demoulding agent studied by EIS and XPS. Corrosion Science, Vol. 45, No. 11, 2003, pp. 2513–2524.10.1016/S0010-938X(03)00076-3Suche in Google Scholar

[23] Shi, Y., B. Yang, X. Xie, J. Brechtl, K. A. Dahmen and P. K. Liaw. Corrosion of Al xCoCrFeNi high-entropy alloys: Al-content and potential scan-rate dependent pitting behavior. Corrosion Science, Vol. 119, 2017, pp. 33–45.10.1016/j.corsci.2017.02.019Suche in Google Scholar
Received: 2024-04-11
Revised: 2024-06-15
Accepted: 2024-06-19
Published Online: 2025-02-18

© 2025 the author(s), 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. Endpoint carbon content and temperature prediction model in BOF steelmaking based on posterior probability and intra-cluster feature weight online dynamic feature selection
  3. Thermal conductivity of lunar regolith simulant using a thermal microscope
  4. Multiobjective optimization of EDM machining parameters of TIB2 ceramic materials using regression and gray relational analysis
  5. Research on the magnesium reduction process by integrated calcination in vacuum
  6. Microstructure stability and softening resistance of a novel Cr-Mo-V hot work die steel
  7. Effect of bonding temperature on tensile behaviors and toughening mechanism of W/(Ti/Ta/Ti) multilayer composites
  8. Exploring the selective enrichment of vanadium–titanium magnetite concentrate through metallization reduction roasting under the action of additives
  9. Effect of solid solution rare earth (La, Ce, Y) on the mechanical properties of α-Fe
  10. Impact of variable thermal conductivity on couple-stress Casson fluid flow through a microchannel with catalytic cubic reactions
  11. Effects of hydrothermal carbonization process parameters on phase composition and the microstructure of corn stalk hydrochars
  12. Wide temperature range protection performance of Zr–Ta–B–Si–C ceramic coating under cyclic oxidation and ablation environments
  13. Influence of laser power on mechanical and microstructural behavior of Nd: YAG laser welding of Incoloy alloy 800
  14. Aspects of thermal radiation for the second law analysis of magnetized Darcy–Forchheimer movement of Maxwell nanomaterials with Arrhenius energy effects
  15. Use of artificial neural network for optimization of irreversibility analysis in radiative Cross nanofluid flow past an inclined surface with convective boundary conditions
  16. The interface structure and mechanical properties of Ti/Al dissimilar metals friction stir lap welding
  17. Significance of micropores for the removal of hydrogen sulfide from oxygen-free gas streams by activated carbon
  18. Experimental and mechanistic studies of gradient pore polymer electrolyte fuel cells
  19. Microstructure and high-temperature oxidation behaviour of AISI 304L stainless steel welds produced by gas tungsten arc welding using the Ar–N2–H2 shielding gas
  20. Mathematical investigation of Fe3O4–Cu/blood hybrid nanofluid flow in stenotic arteries with magnetic and thermal interactions: Duality and stability analysis
  21. Influence on hexagonal closed structure and mechanical properties of outer heat treatment cycle and plasma arc transfer Ti54Al23Si8Ni5XNb+Ta coating for Mg alloy by selective laser melting process
  22. Effect of rare-earth yttrium doping on the microstructure and texture of hot-rolled non-oriented electrical steel
  23. Study on the rheological behavior and microstructure evolution of isothermal compression of high-chromium cast steel
  24. Analysis of CO2–O2 jet characteristics of post-combustion oxygen lance in converter under the influence of multiple parameters
  25. Source-modulated controllable growth and mechanism exploration of 2D MoS2 deposited by NaCl-assisted CVD
  26. Topical Issue on Conference on Materials, Manufacturing Processes and Devices - Part II
  27. Effects of heat treatment on microstructure and properties of CrVNiAlCu high-entropy alloy
  28. Enhanced bioactivity and degradation behavior of zinc via micro-arc anodization for biomedical applications
  29. Study on the parameters optimization and the microstructure of spot welding joints of 304 stainless steel
  30. Research on rotating magnetic field–assisted HRFSW 6061-T6 thin plate
  31. Efficient preparation and evaluation of dry gas sealed spiral grooves
  32. Special Issue on A Deep Dive into Machining and Welding Advancements - Part II
  33. Microwave hybrid process-based fabrication of super duplex stainless steel joints using nickel and stainless steel filler materials
  34. Special Issue on Polymer and Composite Materials and Graphene and Novel Nanomaterials - Part II
  35. Low-temperature corrosion performance of laser cladded WB-Co coatings in acidic environment
  36. Special Issue for the conference AMEM2025
  37. Effect of thermal effect on lattice transformation and physical properties of white marble
https://doi.org/10.1515/htmp-2024-0045
Schlagwörter für diesen Artikel
high-entropy alloy; heat treatment; microstructure; corrosion resistance
Creative Commons
BY 4.0

Artikel in diesem Heft

  1. Research Articles
  2. Endpoint carbon content and temperature prediction model in BOF steelmaking based on posterior probability and intra-cluster feature weight online dynamic feature selection
  3. Thermal conductivity of lunar regolith simulant using a thermal microscope
  4. Multiobjective optimization of EDM machining parameters of TIB2 ceramic materials using regression and gray relational analysis
  5. Research on the magnesium reduction process by integrated calcination in vacuum
  6. Microstructure stability and softening resistance of a novel Cr-Mo-V hot work die steel
  7. Effect of bonding temperature on tensile behaviors and toughening mechanism of W/(Ti/Ta/Ti) multilayer composites
  8. Exploring the selective enrichment of vanadium–titanium magnetite concentrate through metallization reduction roasting under the action of additives
  9. Effect of solid solution rare earth (La, Ce, Y) on the mechanical properties of α-Fe
  10. Impact of variable thermal conductivity on couple-stress Casson fluid flow through a microchannel with catalytic cubic reactions
  11. Effects of hydrothermal carbonization process parameters on phase composition and the microstructure of corn stalk hydrochars
  12. Wide temperature range protection performance of Zr–Ta–B–Si–C ceramic coating under cyclic oxidation and ablation environments
  13. Influence of laser power on mechanical and microstructural behavior of Nd: YAG laser welding of Incoloy alloy 800
  14. Aspects of thermal radiation for the second law analysis of magnetized Darcy–Forchheimer movement of Maxwell nanomaterials with Arrhenius energy effects
  15. Use of artificial neural network for optimization of irreversibility analysis in radiative Cross nanofluid flow past an inclined surface with convective boundary conditions
  16. The interface structure and mechanical properties of Ti/Al dissimilar metals friction stir lap welding
  17. Significance of micropores for the removal of hydrogen sulfide from oxygen-free gas streams by activated carbon
  18. Experimental and mechanistic studies of gradient pore polymer electrolyte fuel cells
  19. Microstructure and high-temperature oxidation behaviour of AISI 304L stainless steel welds produced by gas tungsten arc welding using the Ar–N2–H2 shielding gas
  20. Mathematical investigation of Fe3O4–Cu/blood hybrid nanofluid flow in stenotic arteries with magnetic and thermal interactions: Duality and stability analysis
  21. Influence on hexagonal closed structure and mechanical properties of outer heat treatment cycle and plasma arc transfer Ti54Al23Si8Ni5XNb+Ta coating for Mg alloy by selective laser melting process
  22. Effect of rare-earth yttrium doping on the microstructure and texture of hot-rolled non-oriented electrical steel
  23. Study on the rheological behavior and microstructure evolution of isothermal compression of high-chromium cast steel
  24. Analysis of CO2–O2 jet characteristics of post-combustion oxygen lance in converter under the influence of multiple parameters
  25. Source-modulated controllable growth and mechanism exploration of 2D MoS2 deposited by NaCl-assisted CVD
  26. Topical Issue on Conference on Materials, Manufacturing Processes and Devices - Part II
  27. Effects of heat treatment on microstructure and properties of CrVNiAlCu high-entropy alloy
  28. Enhanced bioactivity and degradation behavior of zinc via micro-arc anodization for biomedical applications
  29. Study on the parameters optimization and the microstructure of spot welding joints of 304 stainless steel
  30. Research on rotating magnetic field–assisted HRFSW 6061-T6 thin plate
  31. Efficient preparation and evaluation of dry gas sealed spiral grooves
  32. Special Issue on A Deep Dive into Machining and Welding Advancements - Part II
  33. Microwave hybrid process-based fabrication of super duplex stainless steel joints using nickel and stainless steel filler materials
  34. Special Issue on Polymer and Composite Materials and Graphene and Novel Nanomaterials - Part II
  35. Low-temperature corrosion performance of laser cladded WB-Co coatings in acidic environment
  36. Special Issue for the conference AMEM2025
  37. Effect of thermal effect on lattice transformation and physical properties of white marble
Jetzt anmelden und 20% sparen
Institutioneller Zugang
Wie funktioniert Authentifizierung?
Gewinner des OpenAthens UX Award 2026
Gewinner des OpenAthens UX Award 2026
Haben Sie eine Idee, wie wir unsere Website verbessern können?
Bitte schreiben Sie uns.
© 2026 De Gruyter Brill
Heruntergeladen am 12.3.2026 von https://www.degruyterbrill.com/document/doi/10.1515/htmp-2024-0045/html
Button zum nach oben scrollen