Late Stage Of Solidification Research Articles

Research on hot cracking in laser welding of Al-contaminated CoCrFeMnNi high-entropy alloys

To study the thermal cracking susceptibility of laser-welded CoCrFeMnNi high-entropy alloys, stainless steel and aluminum alloy plates were each used as backing for welding. The microstructure of the weld and morphology of the fracture were examined. In addition, the chemical compositions of the fractures, the interfacial tension between the CoCrFeMnNi high-entropy alloy and liquid aluminum alloy, and the linear expansion coefficient of the CoCrFeMnNi high-entropy alloy were determined. The results show that when stainless steel is used as the base plate, no cracking is apparent in the weld, and the microstructure is made up of dendrites and equiaxed crystals. Conversely, when an aluminum alloy plate is adopted, solidification cracks are seen at the center of the weld, and the microstructure consists of bright polygonal dendrites scattered in a dark gray matrix. In the later stage of solidification, the contact angle between the Al-dominated low-melt liquid metal and the CoCrFeMnNi high-entropy alloy is about 14.6°, which is distributed in the form of a liquid film between the dendrite of the CoCrFeMnNi high-entropy alloy weld, and the linear expansion coefficient of the high-entropy alloy is 23 × 10−6-25 × 10−6 K−1 in the temperature range of 900–1100 K, which is higher than the thermal expansion coefficient of austenitic stainless steel in this range, and the solidification temperature range is 1000–1400K. Therefore, thermal cracks tend to occur during the solidification process.

Purifying High-Purity Copper via Semi-Continuous Directional Solidification: Insights from Numerical Simulations

High-purity copper is essential for fabricating advanced microelectronic devices, particularly integrated circuit interconnects. As the industry increasingly emphasizes scalable and efficient purification methods, this study investigates the multi-physics interactions during the semi-continuous directional solidification process, utilizing a Cu-1 wt.%Ag model alloy. Coupled simulation calculations examine the spatial distribution patterns of the impurity element silver (Ag) within semi-continuously solidified ingots under varying pulling rates and melt temperatures. The objective is to provide technical insights into the utilization of the semi-continuous directional solidification method for high-purity copper purification. The findings reveal that increasing the pulling rate and melt temperature leads to a downward shift in the solid–liquid interface relative to the mold top during processing. Alongside the primary clockwise vortex flow, a secondary weak vortex emerges near the solid–liquid interface, facilitating the migration of the impurity element Ag toward the central axis and amplifying radial impurity fluctuations. Furthermore, diverse pulling rates and melt temperature conditions unveil a consistent trend along the ingot’s height, which is characterized by an initial increase in average Ag content, followed by stabilization and then a rapid ascent during the late stage of solidification, with higher pulling rates and melt temperatures expediting this rapid ascent. Leveraging these insights, a validation experiment using 4N-grade recycled copper in a small-scale setup demonstrates the effectiveness of the semi-continuous directional solidification process for high-purity copper production, with copper samples extracted at 1/4 and 3/4 ingot heights achieving a 5N purity level of 99.9994 wt.% and 99.9993 wt.%, respectively.

Formation and effect of intermetallic compounds in the vacuum arc melting of titanium/copper alloy

The effect of Ti element content on the precipitation of intermetallic compounds, microstructure and mechanical properties of Ti–Cu alloy samples during vacuum arc melting was studied. The results showed that when the TC4:Cu mass ratio were 1:20, 1:10, and 3:20, the tensile strength of the sample were 638 MPa, 945.5 MPa, 914.9 MPa, the elongation were 21.1 %, 3.5 %, 0.9 %, and the microhardness were Hv 195.6, Hv 259.01, Hv 275.6, respectively. The solidification behavior of the melt pool and the precipitation behavior of IMCs were also studied. When the Ti content exceeds the solid solubility of titanium in copper, dendrite segregation will occur during the solidification process, resulting in the precipitation of a large number of IMCs. The IMCs precipitated in Ti–Cu melting samples include TiCu, Ti3Cu4, TiCu3, and TiCu4. Among them, TiCu4 is precipitated from the solid solution due to the decrease in melt temperature in the later stage of solidification, while TiCu, Ti3Cu4, and TiCu3 are produced by liquid-phase precipitation or transformation reaction of the TiCu phase. TiCu and Ti3Cu4 are the main causes of alloy fracture.

Controllable reinforcement phase distribution at the grain scale via a simple precipitation process

Due to the inability of Zr to refine Al-containing Mg alloys, achieving pronounced grain refinement in cast AZ31 alloy has been a significant challenge for researchers. Surprisingly, we found that the reinforcement phases demonstrated a regular distribution at the grain scale after adding 0.9 wt% Nd and 0.3 wt% Y: Al2RE inside the grains and Al11RE3 agglomerated near the grain boundaries. Additionally, the grain size of AZ31 alloy was significantly reduced from 258 µm to 65 µm. The mechanisms of reinforcement phase distribution and grain refinement were explored through the combination of transmission electron microscope (TEM) and thermal analysis during the solidification process. Al2RE phase precipitates prior to α-Mg, and exhibits a specific orientation relationship with the matrix: 011̅0Mg∥011Al2RE，0002Mg∥22̅2Al2RE. This suggests that Al2RE serves as potentially effective heterogeneous nucleation sites for α-Mg. Moreover, Al11RE3 phase can restrict grain growth in the later stage of solidification. The tensile results show that a regular distribution of the reinforcement phase at the grain scale can not only effectively alleviate stress concentration, but suppress the formation of coarse twins by inducing grain refinement during alloy solidification process, significantly improving the strength and ductility of the alloy.

Certain investigation on feasibility of developing riser less ductile iron castings

The solidification mechanism of ductile iron is a bit complex due to the precipitation of graphite and silicon. These elements change the solidification pattern of cast iron. Density of these elements is less than iron leads to occupying more volume consequently increase the overall metal volume. There are two aspects on this increase in metal volume. One is, reducing this volume increase to reduce the creation of porosities at the earlier stage of solidification and second is, using this volume increase to remove porosity at the later stage of solidification. Proper understanding of this graphite expansion in cast iron solidification will bring insights on reducing or removing of the risers. The current study focus on correlating the net contraction and austenitic liquidus point with shrinkage. The average contraction found through this study is 1.36 % which is more than the net expansion of 0.25 % (without riser) reported in literature. The study found that properly balancing graphite precipitation, pouring temperature and mold strength can enable riserless casting of ductile iron by compensating for liquid contraction through graphite expansion.

Al-Mn-based decagonal quasicrystal in AZ magnesium alloys and its nucleation on Al8Mn5 during solidification

Manganese is added to many magnesium alloys to control impurity iron, but its effects on phase transformations and microstructure formation remain incompletely understood. Here we show that an Al-Mn-based decagonal quasicrystal (d-QC) forms in the late stages of solidification in AZ31 and AZ91 magnesium alloys at relatively slow cooling rates, here down to 0.1 K/s. The d-QC has a periodicity of ∼ 12 Å, grew as decagonal rods and commonly shared interfaces with Al8Mn5 and eutectic Mg17Al12. A reproducible orientation relationship (OR) was measured with Al8Mn5 only, indicating that the d-QC nucleated on Al8Mn5. The OR is consistent with the structural relationship between quasicrystals and gamma brasses and gives the d-QC nucleation advantages over LT-Al11Mn4 during solidification. A subsequent heat treatment at 410 °C caused both Al8Mn5 and the d-QC to transform into LT-Al11Mn4.

In Situ Observation the Effect of Y on the Solidification Process of 7Mo-SASS under a Low Cooling Rate.

The effects of Y on the solidification process of 7Mo super austenitic stainless steel (7MoSASS) under low cooling rate conditions (10 °C/min) were investigated using high-temperature confocal laser scanning microscopy (HT-CLSM). The in situ observation results indicate that Y samples promote an increase in austenite nucleation density. After 10 s of nucleation, the nucleation density increased by 149.53/mm2 for the Y sample. Furthermore, variance analysis indicated that Y addition improved the uniformity of the 7MoSASS solidification microstructure under low cooling rate conditions. The Johnson-Mehl-Avrami-Kolmogorov (JMAK) theory results showed that when the solid phase ratio was 0.5, the nucleation mode of the Y sample transitioned from saturation site nucleation to saturation site nucleation + Avrami nucleation. YAlO3 has a low lattice disregistry value with austenite, making it a suitable heterogeneous nucleation core for promoting the early nucleation of austenite. During the late stages of solidification, Y accumulates in the residual liquid phase, providing a greater degree of compositional undercooling. SEM-EDS analysis showed that Y contributed to the refinement of the 7MoSASS solidification microstructure, with the proportion of precipitated phases decreasing by approximately 7.5%. Cr and Mo were the main elements exhibiting positive segregation in 7MoSASS, and the Cr segregation ratio increased in the Y sample, while the Mo segregation ratio decreased.

Solidification microstructure characteristics and their formation mechanism of K447A nickel-based superalloy for dual-performance blisk

In this paper, the effects of cooling rate after casting and stirring process on γ’ phase, γ / γ’ eutectic phase, MC type carbide morphology and grain structure of K447A alloy turbine blisk were studied systematically. The quantitative relationships between cooling rate, stirring process and γ’ phase, γ / γ’ eutectic phase, MC type carbide and grain size were described in detail. The results show that with the increase of cooling rate, the distribution region of γ / γ ‘eutectic phase from the center of blisk to blade decreases gradually and MC type carbide changes from skeleton to block due to the shorter formation time of eutectic and carbide in the later stage of solidification. Besides, with the decrease of cooling rate, the size of γ’ phase increases under the influence of interfacial strain energy and elastic strain energy, and the morphology of γ’ phase gradually evolves from cuboid to concave cuboid, octet and dendritic. At the same time, due to the synergistic effect of cooling rate and stirring process, the blade part is columnar grain and the central part of the blisk is equiaxed grains. In this paper, the evolution mechanism of γ ‘phase, γ / γ’ eutectic phase, MC type carbide and grain size with cooling rate and stirring process was proposed. The research results would play a key supporting role in precise control during solidification for microstructures and properties of dual-performance superalloy blisk.

Highly oriented microtube arrays of decagonal quasicrystal approximants in Al20Si20Mn20Fe20Ga20 high-entropy alloy

The unique structures of micro/nanotubular materials have received extensive attention, while the micro/nanotubular structures of quasicrystals or quasicrystal-related phases, especially oriented arrays, are rarely found. Here, oriented microtube arrays of high-entropy decagonal quasicrystal approximants are prepared in Al20Si20Mn20Fe20Ga20 alloy by simple melt spinning. Transmission electron microscopy revealed microtubes are mostly composed of alternating arrangements of (1/0, 2/1) quasicrystal approximant domains (lattice constants: a = 0.73 nm, b = 1.23 nm, and c = 2.24 nm) and defective (1/0, 2/1) domains. However, heat treatment leads to the change of the structure and morphology of microtubes. At 873 K, a primitive cubic phase existed, and at 973 K, microtube morphology disintegrated and the (1/0, 2/1)-related domain transformed into complex domains, showing instability. By nanoindentation testing, microtubes show the hardness of 10.9 GPa and the elastic modulus of 189.3 GPa. However, after heat treatment at 873 K, these values decreased to 5.3 GPa and 128.4 GPa, and to 3.2 GPa and 107.9 GPa at 973 K. We demonstrate that the formation of microtubes is mainly related to the temperature gradient, twinning growth of approximant domains, and also the insufficient supply of raw materials in the later stages of solidification.

Formation Mechanism of Secondary Inclusions in Fe-36mass%Ni Alloy Using a Novel Combination Analysis Technique

Controlling the size, number, and composition of secondary inclusions is vital in the production of high-quality steels. In this study, experimental and computational investigation of the relationship between secondary inclusion formation in Fe-36mass%Ni alloy and cooling rate was carried out. Assuming the case of large ingots, solidification experiments using various cooling rates (0.17 to 128 K/min) were employed and the size, number, composition, and distribution of inclusions were analyzed by SEM-EDS automatic inclusion analysis. Like previous studies, inclusion number density increased with increasing cooling rate, while inclusion size decreased with increase of cooling rate. On the contrary, oxide inclusion area fraction was found to have little relationship with the cooling rate and was instead found related with oxygen content of the sample. As a new attempt to investigate the relationship between microsegregation and secondary inclusion formation, a combination of SEM-EDS analysis and EPMA mapping analysis was carried out. By superimposing information of microsegregation and inclusions, it was found that high-Al2O3 inclusions formed during the early stage of solidification, whereas low-Al2O3 inclusions formed during the later stage of solidification. These findings suggest that Al2O3 inclusions formed in the early stage of solidification reacted with the remaining Si-enriched liquid steel and changed into low-Al2O3 inclusions. Experimental results were also confirmed by thermodynamic calculations. Present work made it possible to understand deeper the relationship between microsegregation and secondary inclusion formation.

Effect of dendrite arrays near grain boundary on the competitive growth of converging Ni-based bi-crystal superalloys

The relationship between the arrangement of dendrite array near grain boundary (GB) and the competitive converging dendrites growth in Ni-based superalloys was characterized by the minimum spanning tree method. The results show that the primary dendrite arm spacing near and far away from GB region is different. The dendrite spacing near GB affects the interlacing of convergent dendrites, thus affecting the competitive growth. At the early solidification stage when the spacing is small, the increasing spacing near GB allows the interlacing of convergent dendrites, which leads to the continuous overgrowth of unfavorably oriented (UO) dendrites to favorably oriented (FO) dendrites. However, at the later stage of solidification when the dendrite spacing become larger, the concomitant growth of developed side-branches will hinder the interlacing of convergent dendrites. Consequently, FO-dendrites with superior growth blocks UO-dendrites with directional growth, and even overgrows UO-dendrites.

Solving the problem of solidification cracking during additive manufacturing of CrMnFeCoNi high-entropy alloys through addition of Cr3C2 particles to enhance microstructure and properties

In this study, TiAl and Cr3C2 particles were added to a high-entropy CrMnFeCoNi alloy through powder mixing and selective laser melting (SLM) with the aim of acquiring both high SLM processibility and an excellent combination of high strength and ductility with a post-process aging treatment. By only adding 4 at.% TiAl particles into CrMnFeCoNi, a number of cracks were found in as-printed samples for the processing conditions under investigation, promoted by a considerable increase in solidification range and gradient in the late stage of solidification. However, further addition of 2.5 at.% Cr3C2 particles into (CrMnFeCoNi)96(TiAl)4 reduced the solidification range and gradient, allowing to successfully suppress hot cracking. The as-printed (CrMnFeCoNi)96(TiAl)4 samples are characterized by γ grains each containing a group of cells oriented along a similar direction, with the matrix decorated by a small number of nano-sized Al2O3 and σ particles and the cell boundaries with segregated Ti. The addition of Cr3C2 transformed the segregated Ti at the cell boundaries into discrete TiC nanoparticles. On aging at 650 °C, a high density of long-range ordered domains with considerable B2 and σ precipitates formed. Compared to the SLM-processed CrMnFeCoNi, the as-printed (CrMnFeCoNi)96(TiAl)4 displays a reduced 0.2% yield strength and significantly reduced ductility due to the presence of cracks. Conversely, the as-printed (CrMnFeCoNi)96(TiAl)4 + Cr3C2 samples showed a slightly enhanced yield strength and considerably improved UTS. Aging significantly improves both strength properties while maintaining the good ductility. The long-range ordered domains and precipitation clearly are effective in impeding dislocation motion and can be considered to be the prime source of the increased strength of the dual-particle containing alloy.

Precipitation behavior of TiN in solidification of 20CrMnTi under continuous casting conditions

This paper focused on the relationship between the precipitation of TiN and the continuous casting process of 20CrMnTi billet. A reliable cross scale simulation combining the heat transfer, solute micro-segregation, and TiN precipitation was carried out. Results show that for a specific site, the cooling rate in the mushy state increases with the solidification proceeding, especially in the later stage of solidification. The closer to the center of billet, the lower the initial cooling rate is. However, the cooling rate in the later stage of solidification near the center of billet is higher than that of the intermediate site. The solidification path of 20CrMnTi at 20, 40, and 60 mm below the inner arc surface is L → L + δ → L + δ + γ → L + γ → γ, and the peritectic reaction occurs at the solid fraction of 0.81. The solute segregates more severe as the site moves to the inner billet, especially among the coarse equiaxed dendrites at 60 mm. The precipitation of TiN just slows down the enriching rate of Ti in the liquid phase, but causes the concentration of N declining. The predicted maximum sizes of TiN are 6.128, 7.836, and 7.593 μm at 20, 40, and 60 mm, and its tendency is consistent with the measurements in the billet. With the decrease of N's initial content, the formation of TiN is postponed to higher solid fraction, and TiN becomes smaller. Moreover, the decisive factor for TiN's size at 40 and 60 mm changes from the concentration difference to the growth time. In addition, increasing the secondary cooling intensity can also refine TiN.

Cracking mechanism and its susceptibility to scanning speed during laser power bed fusion processed high-strength 2024Al alloy

Laser powder bed fusion (L-PBF) is a promising technique for fabricating high-performance complex aluminum (Al) alloy components. However, conventional high-strength wrought Al alloys that are processed using L-PBF have limited application owing to their poor cracking resistance. To investigate the cracking mechanism, L-PBF was used to fabricate a 2024Al alloy. The resultant microstructure exhibited severe hot cracking, which occurred at grain boundaries with a high angle in both solidification and liquation cracks. Increasing the scanning speed increased the susceptibility to cracking. The effect of scanning speed on the eutectics content of Al2Cu and Al2CuMg and the residual stress in as-fabricated samples are discussed. Crack elimination at a low scanning speed could be ascribed to the lower thermal stresses and adequate liquid feeding during the late stage of solidification. In addition, based on the RDG (Rappaz-Drezet-Gremaud) model, a cracking susceptibility map was produced, in which the cracking susceptibility was determined to increase with an increase in the solidification rate, in agreement with experimental observation.

Effect of Dynamic Soft Reduction Range and Amount on Central Segregation in Bloom and the Resulting Microstructure in the Rod of GCr15‐Bearing Steel

Composition uniformity is essential to the quality, stability, and fatigue life of bearing materials. In the current study, various calculations and measurement methods are implemented to obtain the high‐temperature physical properties of GCr15‐bearing steel. Combined with a validated transient heat transfer model, two cases with different dynamic soft reduction (DSR) ranges and amounts are designed for industrial trials. The defects, carbon contents, and carbides in the bloom center and the carbon contents and microstructure in the rod center are compared. The results show that the reasonable matching of casting speed and cooling water flux in continuous casting could reduce the total content of enriched carbon at the middle and late stages of solidification. Setting a reasonable DSR range (solid fraction: 0.3–1.0) and applying a heavy DSR amount could effectively improve central segregation in bloom and the resulting microstructure in the rod.

Effect of Zn content on hot tearing susceptibility of LPSO enhanced Mg–Znx–Y2–Zr0.06 alloys with different initial mold temperatures

The critical temperature (Thci) corresponding to the load relaxation measured during the solidification of alloy in a ‘T′-shaped mold is introduced into the Clyne-Davies’ model, so that it can be used to predict the hot tearing susceptibility (HTS) of alloy under non-equilibrium cooling. Then, the improved model is applied to study the HTS of Mg–Znx–Y2–Zr0.06 (x = 0.5, 1 and 1.5 at%) alloys under two initial mold temperatures, i.e., two cooling rates. It is found that HTS is very sensitive to both Zn content and initial mold temperature, and the increase in Zn content or initial mold temperature can reduce HTS of the alloy. However, their micro mechanisms are different. The reason for the decrease in HTS with the increase in Zn content is the decrease in the dendrite coherency temperature. Specifically, the ratio of unconstrained feeding stage to intergranular feeding stage increases, and the intergranular liquid phase with eutectic composition increases in the later stage of solidification. The HTS decreases with the increase in the initial mold temperature because the solidification shrinkage stress is relieved. Consequently, the residual liquid phase between the grains can be fed in a more timely manner.

Formation Sequence of Compounds in AZ91‐0.9Ce Alloy and Its Role in Fracture Process

AZ91‐0.9Ce alloy with a thickness of 8 mm is prepared by die casting. The formation process of main compounds in the alloy, the role of main compounds in fracture process, the main crack source, and crack propagation path of the alloy are studied. Results show that AZ91‐0.9Ce alloy is mainly composed of α‐Mg matrix, Mg17Al12 compound, Al4Ce compound, and a small amount of Al–Mn–Ce ternary compound. Among them, Al4Ce is formed prior to the Mg17Al12 compound. Mg17Al12 is formed by eutectic reaction, and Al–Mn–Ce ternary compound is formed at a later stage of solidification. Mg17Al12 and Al4Ce are the main crack sources of the alloy during the fracture process. Crack locations in the alloy mainly include grain boundaries, phase boundaries, and Mg17Al12 and Al4Ce compounds. The fracture mechanism of the alloy is that with the increase of load cracks occur at Mg17Al12 and Al4Ce compounds and connect with each other through intergranular and a small amount of transgranular to form the main crack. With the load continues to increase, the main crack gradually expands until alloy fracture failure. The continuous network distribution along grain boundaries of the Mg17Al12 compound is an important reason for intergranular fracture.

Crystal Mush Growth and Collapse on a Steep Wall: The Marginal Border Series of the Skaergaard Intrusion, East Greenland

Abstract The Skaergaard Intrusion of East Greenland solidified as a closed system, with the development of progressively more fractionated material at the roof, floor and vertical walls of the magma chamber. We argue, using field observations of the exposed western margin together with detailed microstructural and geochemical analysis, that the mush on the vertical walls of the Skaergaard Intrusion reached a maximum thickness of ~180 m, and was highly unstable. Material was lost both continuously, due to non-retention of poorly consolidated material, and during episodic collapse events. The almost complete absence in the wall rocks of material formed in LZc times (following the saturation of the bulk magma in Fe-Ti oxides) was likely to have been caused by a collapse event, perhaps related to faulting of the actively extending Greenlandic margin. A second major collapse of the MBS occurred during the later stages of solidification, with the greatest loss of material occurring in a region of the wall with an unusually thick mush, creating a transient and localised increase in the thickness of the floor mush. This work demonstrates the importance of vertical walls in supplying loose, disaggregated material to form mobile magmatic slurries that may contribute to floor cumulates or be entrained and erupted in long-lived systems.

Transient liquid phase bonding of Ni3Al based superalloy using Mn–Ni–Cr filler

A new 70Mn–25Ni–5Cr (wt. %) filler with no traditional melting-point depressants (MPDs) of Si/B was used for transient liquid phase (TLP) bonding a directionally solidified (DS) superalloy based on Ni3Al intermetallic compound (IMC) at 1150 °C, a pressure of 2 MPa for 10–120 min. Experimental results show that the joint can be divided into 3 zones, isothermally solidified zone (ISZ), athermally solidified zone (ASZ) and diffusion-affected zone (DAZ), which was similar to microstructure of typical TLP joint bonded by Ni based filler. The joint microstructures were mainly composed of γ-Ni, γ′-Ni3(Al, Ta), MC and M23C6 carbides. Besides, in the ISZ, due to the enrichment of Al, which diffused from the base metal (BM), strip-shaped Ni(Mn, Al) phases formed in such region. The ASZ included γ-Ni and compounds of “equiaxed Ni(Mn, Al) + acicular Ni3Ta” owing to the composition segregation during the later stage of solidification. Moreover, as the bonding time increased, the volume fraction of Ni(Mn, Al) and MC carbides decreased owing to homogenization of alloying elements. After bonding for 120 min, sufficient isothermal solidification (IS) of filler can also decrease segregation of Mn/Al in front of the S/L interface and the Ni(Mn, Al)+Ni3Ta compounds were eliminated almost. Thus, the highest tensile strength was 816.9 MPa of the TLP joint of 120 min, which has been equivalent to that of BM (812 MPa). However, due to the existence of a few residual large MC carbides in the joint, which can induce the stress concentration and decreased the ductility of the joints, the highest joint elongation of 4.4% was only about 40% of the BM.

Thermodynamic Calculation and Characterization of Carbide Precipitation in Laser-Deposited Material for High-Speed Steel Alloy

The laser cladding of the T15 high-speed steel (HSS) was accomplished and its typical microstructure was determined. The microstructure characterization of the clad layer showed three phases of microstructure, planar, cellular and equiaxed growth zones. Electron probe micro-analyzer (EPMA) showed high content in alloying elements at the cellular and equiaxed zones that contained V, C, Cr and W. Further, the analysis at the inter-granular zone presented the highest concentration in elements such as Mo, Cr and W. This showed the presence of carbides which were identified as MCI and M6C at the cellular zone, and M7C3 and M23C6 at the equiaxed and inter-granular zones. The precipitation characterization along the line starting from the substrate and passing through the clad layer identified the austenite matrix and revealed the fluctuation in the alloying elements content, where its amplitude and count increased while passing through the planar zone and hitting the equiaxed zone. Equilibrium phase diagram thermodynamic calculation proved the presence of MCI, M6C and M23C6 which precipitated respectively as the solidification proceeded. The M6C carbide was rich in Fe and W with the presence of V and Cr. MCI carbide had high content of C and V also with dissolved content of W and Cr. Finally, M23C6 carbide contained high amounts of W, Cr and Mo. Scheil–Gulliver simulation model showed the presence of M6C and MCI similar to the equilibrium phase diagram results, additionally, two carbides were revealed and identified as M7C3 and MCII carbides. The M23C6 was absent from the Scheil–Gulliver model. This is due to the assumption that in the Scheil–Gulliver model, the solid stage has no diffusion, and the M23C6 was proved to precipitate in later stages of solidification as shown in the equilibrium phase diagram results. Finally, transmission electron microscopy (TEM) and x-ray diffraction (XRD) showcased the presence of the carbides predicted from the equilibrium phase diagram.