# Structural Particularities, Prediction, and Synthesis Methods in High-Entropy Alloys
## 3 Synthesis Methods and Their Influence on the Structure and Properties of HEA Alloys
### Synthesis Methods for HEA Alloys
The melting and casting method offers several benefits, including being time-efficient, cost-effective, and energy-saving. However, high-temperature segregation poses challenges, leading to the formation of dendritic and interdendritic structures. The cooling rate during solidification is crucial in shaping the microstructure and properties of the material. Various studies have shown that the growth of dendrites, the volume fraction in the interdendritic region, and the distribution of alloying elements are significantly influenced by the cooling rate [71]. Induction melting is based on the induction heating characterized by the Joule effect of induced currents resulting from the penetration of an electromagnetic field into a conductive material placed in a time-varying magnetic field. The energy transformation process is presented in Figure 5. Induction heating of a body involves three successive physical phenomena:  
* The transfer of electromagnetic energy from the coil to the body to be heated;
* The generation of heat in the material as a result of the Joule effect;
* The transfer of heat through thermal conduction throughout the entire mass of the body. Multicomponent High-Entropy Alloys (HEAs) are commonly produced by conventional induction melting or vacuum arc melting, followed by casting, which requires repeated remelting to achieve chemical homogeneity [72]. Typically, conventional casting with cooling rates of 10-20 K\(\cdot\)s\({}^{-1}\) leads to substantial phase separation during HEA production, often requiring additional post-treatment to refine the microstructure and achieve the desired properties (Figure 6). Moreover, the inherent complexity and precise  
Figure 4: Summary of HEA fabrication routes. Figure 5: The chain of energy transformations in an electromagnetic induction installation. control required to produce bulk homogeneous alloys remains challenging for traditional manufacturing methods in the industry. The melting temperatures of non-ferrous alloys vary widely due to the differing fusibilities of their constituent metals. Based on their melting points, these metals can be categorized as follows:  
* Easily fusible metals, which melt at temperatures below 500 \({}^{\circ}\)C (e.g., Sn, Pb, Cd, Zn, etc.) * Metals with medium melting temperatures, ranging from 500 \({}^{\circ}\)C to 1000 \({}^{\circ}\)C (e.g., Al, Mg, Sb, Ag, etc.) * Metals with high melting temperatures, ranging from 1000 \({}^{\circ}\)C to 1500 \({}^{\circ}\)C (e.g., Cu, Au, Ni, Co, Mn, etc.) * Refractory metals, which have melting temperatures above 1500 \({}^{\circ}\)C (e.g., Cr, Zr, Hf, Ti, W, Mo, etc.) Under isobaric conditions, the phase transformation of metals during melting is isothermal [73]. Since melting is a process of transitioning from one condensed state to another, the pressure variations that may occur under real conditions are not significant enough to alter the phase transformation temperature. Calculations performed using the Clausius-Clapeyron equation yield negligible variations in melting temperature based on the pressure within the melting aggregates.