Mechanical Properties Of Al0 Research Articles

Effects of Ti Content on the Microstructure and Mechanical Properties of Al0.2CoCrFeNi2Tix High-Entropy Alloys

Effects of Ti Content on the Microstructure and Mechanical Properties of Al0.2CoCrFeNi2Tix High-Entropy Alloys

Effect of annealing temperature on the microstructure and mechanical properties of Al0.2CrNbTiV lightweight refractory high-entropy alloy

The DSC analysis and heat treatment of the newly proposed Al0.2CrNbTiV lightweight refractory high-entropy alloy prepared by vacuum arc melting was investigated, and the evolutions of the microstructure and mechanical properties of the alloy after homogenization annealing at 650 °C, 850 °C and 1050 °C for 12 h were analyzed. The results show that the Al0.2CrNbTiV high-entropy alloy could maintain stable BCC solid solution structure from room temperature to 800 °C. The alloy annealed at 650 °C exhibited simple BCC structure with coarse equiaxed grains; after annealing at 850 °C, fine acicular and irregular block-like C14 Laves phases were uniformly precipitated in the grain and grain boundaries, meanwhile, the C14 Laves phase get coarser with the annealing temperature increased to 1050 °C. With the increase of annealing temperature, the microhardness of the Al0.2CrNbTiV alloy increased first and then decreased, reaching the maximum value of 692 HV after annealing at 850 °C. Due to the high dislocation density and the formation of kink bands, the alloy annealed at 650 °C showed a good combination of plastic and strength, with the work hardening ability strengthened simultaneously, the compressive yield strength could be up to 1454 MPa, with strain >50 %. Due to the precipitation of the hard and brittle C14 Laves phase, the load-bearing capacity of the alloy was reduced after annealing at 850 °C and 1050 °C. However, the wear resistance of the alloy also improved with the presence of the hard phase. The friction coefficient of Al0.2CrNbTiV alloy annealed at 650 °C is 0.67, with the abrasive wear acting as the main wear mechanism, and the alloy after annealing at 850 °C shew the best wear resistance, with the friction coefficient of 0.63, and delamination wear mechanism.

Effect of crystallographic orientation on mechanical properties of Al0.25CoCrFeNi high entropy alloy under tension

The deformation behavior of single-crystal materials is closely related to the crystallographic orientation. However, there are few simulations and experimental studies on the effect of crystallographic orientation on the tensile properties of single-crystal AlxCoCrFeNi high entropy alloys (HEAs). Molecular dynamics simulations were used to analyze the mechanical properties and structural variations of Al0.25CoCrFeNi HEAs with different crystallographic orientations under tension. Prior to yielding, elastic softening occurred in [111], [110] and [11̅0]-oriented HEAs, except for [100]-oriented HEA. During plastic deformation, [100]-oriented HEA had high strength and flow stress due to the low Schmid factors of leading partial dislocations and multiple activatable slip systems. [111]-oriented HEA also showed high strength and flow stress, which were attributed to the low Schmid factors of the activatable slip systems and the existence of incomplete stacking fault tetrahedrons. Both [110]- and [11̅0]-oriented HEAs showed low strength, but the presence of the secondary increased stress suggested they had good plasticity. The difference between them was that [110]-oriented HEA was easier to form hexagonal close-packed lamellae and experienced secondary yielding at larger strain. This suggested that different crystallographic orientations in the non-tensile direction also affected the mechanical properties.

The Effect of Heat Treatment on the Microstructure and Mechanical Properties of Al0.6CoFeNi2V0.5 High Entropy Alloy

Al0.6CoFeNi2V0.5 high entropy alloy was successfully designed and prepared via the nonconsumable arc-melting process, and it was annealed at 600 °C, 800 °C, and 1000 °C for 4 h. Its microstructure and mechanical properties were studied. The as-cast alloy consisted of FCC and BCC phases, and no phase transformation occurred during annealing at 600 °C. Hard Al3V-type metal compounds precipitated during annealing at 800 °C, and BCC particles precipitated in the FCC matrix during annealing at 1000 °C. After annealing, the strength and hardness of Al0.6CoFeNi2V0.5 high-entropy alloy both showed a decreasing trend, because the annealing process eliminated the internal stress in this alloy. However, as the annealing temperature increased, the strength and hardness of the Al0.6CoFeNi2V0.5 high-entropy alloy samples gradually increased. This is because the hard Al3V metal compounds precipitated when the annealing temperature was 800 °C, which produced the “second phase strengthening” effect. At 1000 °C, the larger volume fraction of the hard and fine BCC phase (21.81%) diffusely precipitated; the precipitation of this BCC phase not only produced a “second phase strengthening” effect, which also resulted in “solid solution strengthening”, ultimately exhibiting enhanced hardness and strength. These findings have important theoretical reference value for the study of the microstructure and mechanical properties of high-entropy alloys. And, this study plays a significant role in promoting the research and development of new component materials that bear compressive loads, such as columns in large factory buildings, supports for cranes, and clamping bolts for rolling mills in practical mechanical engineering.

Construction of multiscale secondary phase in Al0.25FeCoNiV high-entropy alloy and in-situ EBSD investigation

Developing high-entropy alloys (HEAs) faces challenges owing to the inherent strength-ductility trade-off. This study systematically investigated the microstructure and mechanical properties of Al0.25FeCoNiV face-centered cubic (FCC) and body-centered cubic (BCC) duplex HEA, subjected to 70% cold rolling and annealing at various temperatures. The mechanism of the nonlinear effect of the annealing temperature on precipitation in duplex HEA was investigated. An economical and efficient thermo-mechanical processing route was developed to construct a multiscale BCC secondary phase. After 70% cold rolling and annealing at 1373 K, the yield strength (YS), ultimate tensile strength, and fracture elongation were 750 MPa, 1169 MPa, and 46.5%, respectively. This demonstrates superior strength-ductility coordination. In-situ electron backscatter diffraction (EBSD) tensile experiments were performed using a self-designed device to observe the dynamic evolution of the grain orientation and grain boundary distribution under diverse strain conditions. The influence of the multiscale BCC secondary phase on the mechanical properties was comprehensively investigated. The findings suggested that the exceptional mechanical performance was attributed to the coupled mechanism of multistage hetero-deformation-induced (HDI) strengthening and strain hardening produced by the multiscale BCC phase. Quantitative calculations revealed that the HDI strengthening (420 MPa) contributed over 50% to YS. This study lays a solid theoretical foundation for optimizing process parameters and innovating high-performance HEAs for engineering applications.

Microstructure and mechanical properties of Al0.5CoCrFeNi HEA prepared via gas atomization and followed by hot-pressing sintering

Pre-alloyed Al0.5CoCrFeNi high-entropy alloy (HEA) powders were prepared via gas atomization and followed by hot-pressing sintering (HPS) at 1200 °C for 1 h to fabricate bulk materials. The phase stability, microstructure evolution and mechanical properties of Al0.5CoCrFeNi HEA were mainly investigated. Results indicated that the atomized powders exhibited a fine-grained FCC + dendritic-like ordered BCC (B2) dual-phase structure. Rapid solidification was favorable to the metastable B2 phase formation during gas-atomization. Partial of the dendritic-like B2 phase dissolved after annealing (>600 °C), resulted in a homogeneous dual-phase structure with irregular B2 phase dispersed in the FCC matrix. The homogeneous structure was “inherited” in the sintered bulks and coarsened after HPS. Tensile test results suggested that the sintered bulks possessed excellent comprehensive mechanical properties with yield strength, ultimate tensile strength and elongation of 587.3 ± 18.7 MPa, 960.2 ± 23.6 MPa and 32.6 ± 5.1%, respectively. The excellent mechanical response during deformation was mainly attributed to the synergistic deformation of the FCC/B2 phase and considerable back stress hardening mechanism.

Macrostructure, Microstructure, and Mechanical Properties of Al0.2CoCrFeNi High-Entropy Alloy Produced by Vacuum Induction Melting

Macrostructure, Microstructure, and Mechanical Properties of Al0.2CoCrFeNi High-Entropy Alloy Produced by Vacuum Induction Melting

The influences of vanadium addition and temperature on the microstructure, and mechanical properties of Al0.1CoCrFeNiVx multi-principal element alloys

The study aimed to examine the crystal structure, microstructure, microhardness, and tensile properties of Al0.1CoCrFeNiVx (x = 0.0, 0.2, 0.4, 0.6, 0.8, 1.0) multi-principal element alloys. Both Al0.1CoCrFeNi and Al0.1CoCrFeNiV0.2 alloys were single FCC phase solid solutions. σ-phase precipitated in Al0.1CoCrFeNiV0.4 alloy. The volume fraction of σ-phase increased as V content increased from x = 0.4 to 1.0. The volume fraction of σ-phase in Al0.1CoCrFeNiV alloy was found to be 48.4 vol%. It was shown that to predict the phase composition of multi-principal element alloys containing σ-phase employing solid solution formation model, coupling it with criteria of σ-phase formation was necessary. Moreover, when the V content was x ≤ 0.4, the alloys showed good toughness and ductility (> 49%). However, a continuous increase in V content led to a higher volume fraction of σ-phase, which enhanced the strengthening/hardening effect until reaching the embrittlement threshold. At x = 0.4, the alloy exhibited a better balance between strength and plasticity. Uniaxial tensile tests were performed on the annealed Al0.1CoCrFeNiV0.4 alloy at different temperatures. Results suggested that the alloy retains excellent plasticity (> 45%) at 500 ℃. Nevertheless, it exhibited a decrease in strength and plasticity with elevated temperatures. The addition of V caused a significant increase in ultimate strength and elongation at mid-temperatures (500–700 ℃) compared to Al0.1CoCrFeNi alloy. The engineering stress-strain curves of the Al0.1CoCrFeNiV0.4 alloy displayed serrated flow at temperatures from 300 ℃ to 700 ℃. The serration type transitioned from A-type to C-type as the temperature rose.

Effects of Sc addition on microstructure, phase evolution and mechanical properties of Al0.2CoCrFeNi high-entropy alloys

Al0.2CoCrFeNiScx (x=0, 0.1, 0.2 and 0.3, molar fraction) alloys were prepared by arc melting. The effects of Sc addition on the microstructure, phase evolution and mechanical properties of Al0.2CoCrFeNiScx alloys were investigated. The results showed that Sc could refine grain size, change phase type and improve mechanical properties. The grain size of Al0.2CoCrFeNiSc0.3 alloy (8.5 μm) was reduced by approximately 50.6% compared to that of Al0.2CoCrFeNiSc0.1 alloy (17.2 μm). The crystal structure evolved from a single FCC phase to a mixed phase including two types of FCC phases and one type of BCC phase. The FCC phase mainly appeared in the regions of (Co, Cr, Fe)- rich dendrites and (Ni, Sc)-rich interdendrites; while the BCC phase was mainly located in the region of (Al, Ni)-rich interdendrites. The yield strength increased from 167 to 717 MPa as the x value in Al0.2CoCrFeNiScx alloy increased from 0 to 0.3, improved by 329.3%, which could be attributed to grain size strengthening, solid solution strengthening and phase evolution.

Effect of Ti on microstructure and mechanical properties of Al0.8Nb0.5TixV2Zr0.5 refractory complex concentrated alloys

In this study, lightweight Al0.8Nb0.5TixV2Zr0.5 refractory complex concentrated alloys with different Ti contents (x = 0.4, 0.8, 1.2, and 1.6) are fabricated via vacuum arc melting. The effects of Ti on microstructurale evolution, density, and mechanical properties at room and elevated temperatures are investigated. The Al0.8Nb0.5TixV2Zr0.5 alloys are composed of a BCC solid solution matrix and a C14-Laves (hexagonal) phase, and the volume fraction of the BCC phase increases as the Ti content increases from 63.48% to 90.97%. The density decreases from 5.70 to 5.42 g/cm3, whereas the hardness first increases and then decreases in the range of 625.2 to 669.5 HV. The results of compression test at different temperatures show that the yield strength and deformability of the Al0.8Nb0.5TixV2Zr0.5 alloys first increases and then decreases, and that the alloys show good phase stability when the Ti content is 1.2. The compressive yield strength of Ti1.2 alloy is 1848 MPa at room temperature, 1507 MPa at 673 K, and 1068 MPa at 1073 K. The increase in yield strength is due to various strengthening mechanisms caused by the addition of Ti, including the solid-solution strengthening effect caused by severe lattice distortion, the decrease in the valence electron concentration, and the grain boundary strengthening effect caused by grain size reduction. The present study is an example of a systematic investigation into the effects of elements on the structure and properties of refractory complex concentrated alloys through alloy design, which is expected to facilitate the design of lightweight refractories and their compositions.

Microstructure evolution and mechanical properties of directionally solidified Al0.5CoCr1.3FeNi1.3(Ti, Si, B, C)0.3 multiphase complex concentrated alloy

Microstructure evolution and mechanical properties of Al0.5CoCr1.3FeNi1.3(Ti, Si, B, C)0.3 multiphase complex concentrated alloy (CCA) prepared by directional solidification combined with quenching during solidification (QDS) technique were studied. The directionally solidified (DS) samples were prepared at constant growth rates V ranging from 2.78 × 10−6 to 5.56 × 10−5 m/s, the constant temperature gradient in liquid at the solid-liquid interface of GL = 16.5 × 103 °C/m and then quenched at a cooling rate of about 50 °C/s. The solidification of the studied CCA begins with the growth of columnar FCC(A1) dendrites and is finalised by the formation of a multiphase microstructure in the interdendritic region. The DS samples subjected to isothermal annealing at 900 °C for 25 h show a strong brittle-ductile transition (BDT) behaviour characterised by brittle-ductile transition temperature (BDTT) between 650 and 700 °C at a strain rate of 1 × 10−4 s−1. The tensile deformation curves show only a strain hardening stage at test temperatures up to 650 °C. At temperatures ranging from 750 to 900 °C, the alloy shows anomalous strain hardening behaviour characterised by one strain hardening stage and three well-distinguished strain softening stages.

Effect of heat treatment on microstructure and properties of Al0·5CoCrFeNi high entropy alloy fabricated by selective laser melting

In this study, heat treatment as a post processing was used in order to improve the microstructures and mechanical properties of Al0·5CoCrFeNi high entropy alloy (HEA), which fabricated by selective laser melting (SLM). Compared to the microstructure of SLM-ed Al0·5CoCrFeNi HEA, the strengthening the weakening mechanisms of HEA at different heat treatment temperatures are figured out. Heated at 1073 K for 4 h, the SLM-ed Al0·5CoCrFeNi HEA shows the 1419 MPa tensile strength. With increasing heat treatment temperature from 1073 K to 1673 K. The content of BCC phase decreases from 34.4% to 14.6%. The average size of BCC phase at grain boundaries increases from 0.497 μm to 2.271 μm, and the average size of BCC phase inside the grains increases from 0.037 μm to 1.216 μm. Moreover, dislocation network disappearance and recrystallization occur at 1173 K and 1373 K, respectively. The boundaries of the dislocation network, as the nucleation sites of precipitation, promote the formation of precipitated phases and form dislocation network wrapped by precipitated phases at 1073 K. The precipitated phases and the dislocation network wrapped by precipitated phases increase the tensile strength of SLM-ed HEA by 65.8%. The low dislocation density in the recrystallized grains change the morphology of the precipitated phases, and the aspect ratio of the BCC phases increases, which made the HEA still maintain a certain tensile strength at 1673 K.

Experimental and numerical investigation of interface and mechanical properties of Al0.3CoCrFeNi/304L explosively weld composite plate

High entropy alloys (HEAs) have gained attention for their excellent properties, but research on combining them with conventional metals is limited. This study manufactured Al0.3CoCrFeNi/304L composite plates using explosive welding. Welding parameters were determined based on the theoretical weldability window. The detonation process and interface were analyzed using an advanced SPH-FEM algorithm. Interface morphology was characterized using OM, EDS, and EBSD, and mechanical properties were tested. Materials near the interface experienced extreme conditions, resulting in severe plastic deformation and wave interface generation. Interface inhomogeneity wase caused by unsteady detonation and inclined collision. Collision velocity predicted by the SPH-FEM model matched theoretical calculations, and the predicted interface agreed with experimental results. Increased explosive charge led to more intense interface undulation and a thicker diffusion layer. EBSD showed a single-phase structure with non-uniform elements at the nanometer scale. The interface exhibited the highest deformation and grain recrystallization, along with plastic deformation and texture. Mechanical tests revealed that larger wave interfaces had higher hardness, improved tension, bending, and impact toughness, but worse shear performance. Explosive welding proved effective for achieving high-quality bonding between HEAs and conventional metals, offering promising possibilities for HEA and traditional metal composites.

Microstructure and mechanical properties of Al0.4Co0.5V0.6FeNi high-entropy alloys processed by homogenization treatment

Al0.4Co0.5V0.6FeNi high-entropy alloys (HEAs) are fabricated by the vacuum arc melting method and homogenization treatment (HT) at 1000, 1100 and 1200 °C for 5 h (samples denoted as HT-1000, HT-1100 and HT-1200, respectively), followed by water quenching. The microstructural characteristics and mechanical properties of the HEAs are investigated by a combination of optical, scanning and transmission electron microscopy, X-ray diffraction and tension tests. The solidification of the Al0.4Co0.5V0.6FeNi HEAs is calculated using Pandat software to show that the FCC phase forms in the liquid phase, which then undergoes a eutectic reaction to form the FCC and BCC/B2 phases. The Al0.4Co0.5V0.6FeNi HEAs exhibit a typical eutectic microstructure with an alternating lamellar structure. Compared with that in the as-cast state, the volume fraction of the FCC phase in the HT state increases from 53.16% to 60.75% and the yield strength of the HT-1200 alloy increases by ∼27.5% with increasing homogenization temperature. Fine small spherical and ellipsoidal nanoprecipitates are uniformly distributed within the FCC matrix. These FCC phase nanoprecipitates become the most important factor contributing to the yield strength.

Microstructure and properties of Al0.5NbTi3VxZr2 refractory high entropy alloys combined with high strength and ductility

Novel lightweight Al0.5NbTi3VxZr2 (x = 0.5, 1.0, 1.5) refractory high entropy alloys were synthesized by vacuum arc melting. The microstructure evolution and mechanical properties of Al0.5NbTi3VxZr2 alloys were analyzed. All Al0.5NbTi3VxZr2 alloys have a single BCC structure, and the addition of V does not change the microstructure of the alloys. At elevated temperatures, V1.0 alloy shows good phase stability, and the compressive yield strength of V1.0 alloy is 898 MPa at room temperature, 706 MPa at 873 K, and 110 MPa at 1073 K, respectively. Al0.5NbTi3VxZr2 alloys reveal excellent compression deformability, all samples can be compressed to more than 50% strain at room and elevated temperatures without fracture. At room temperature, V1.0 alloy still possesses the best tensile properties, with the yield strength of 694 MPa. The enhancement strength is due to the addition of V element with small atomic radius, which is caused by a variety of strengthening mechanisms, including solid solution strengthening and grain refinement strengthening. Most of the reported Al–Nb–Ti–V–Zr system refractory high entropy alloys have poor deformability at room temperature, and most of the work is focused on their compression properties. The Al0.5NbTi3VxZr2 refractory high entropy alloys prepared in the present work not only have excellent compression deformability, but also excellent tensile properties. Our present study not only promotes the development of toughening Al–Nb–Ti–V–Zr system refractory high entropy alloys to challenge engineering applications, but also provides guidance for the design of lightweight high temperature materials with a variety of strengthening mechanisms.

Microstructure characteristics and mechanical properties of Al0.25CrFeNi1.75Cux high-entropy alloys

In this work, we study the microstructural evolution and mechanical properties of Al0.25CrFeNi1.75Cux (x = 0–0.7) high entropy alloys (HEAs). The microstructural analysis confirmed that high Cu doping altered the microstructure of alloys and evolved from single FCC phase to FCC matrix and AlCu-type phase characteristics. Al0.25CrFeNi1.75Cux alloys exhibited typical dendrite morphology, and at the high doping of Cu content, the average size of the dendrites and secondary dendrite arm spacing was significantly decreased. The mechanical properties of the Al0.25CrFeNi1.75 alloy with different Cu content were studied by tensile tests. When Cu addition concentration increases from 0 to 0.7, the yield strength and the ultimate tensile strength increased by 35.4% and 12.1%, respectively. However, the elongation decreased by 47.2%. Enhanced mechanical characteristics were obtained due to a combination of the fine grain strengthening, the second-phase hardening of AlCu-rich precipitation, and the solid-solution strengthening.

Effect of Cryogenic Treatment on Microstructure and Mechanical Properties of Al0.6CrFe2Ni2 Dual-Phase High-Entropy Alloy

The contradiction between strength and ductility limits the application of high-entropy alloys (HEAs). To simultaneously improve the strength and ductility of HEAs, the cryogenic treatment was proposed and applied in this paper. The Al0.6CrFe2Ni2 HEA with dual-phase structure was selected as the experimental material for cryogenic treatment. The microstructure and mechanical properties of the HEA in an as-cast and cryogenically treated state were analyzed in detail. The results showed that the grain size of equiaxed crystal in the alloy decreased continuously by prolonging the cryogenic treatment time, and the average value was 44.6 μm for the cryogenically treated HEA at the time of 48 h, which was 46.5% lower than that of the as-cast alloy. The number and size of ordered body-centered cubic (B2) spherical nanophases embedded in the body-centered cubic (BCC) structured inter-dendritic region, however, increased continuously by extending the cryogenic treatment time. The cryogenic treatment also made more slip systems activate, cross-slip occurred in the alloy, and a large number of stacking faults were found in the transmission electron microscopy (TEM) microstructure for the alloy that underwent a long time in cryogenic treatment. The yield strength of the Al0.6CrFe2Ni2 HEA was gradually increased with the increase in cryogenic treatment time, and the maximum yield strength of the 48 h cryogenically treated alloy was 390 MPa, which was 39.3% higher than that of the as-cast. This increase in mechanical properties after cryogenic treatment was attributed to the refinement of grains and the large precipitation of nanophases, as well as the appearance of cross-slips and stacking faults caused by cryogenic treatment.

Effect of TiO2 nano-ceramic particles on microstructure and mechanical properties of Al0.4CoCrFe2Ni2 high-entropy alloy

Al0.4CoCrFe2Ni2 high-entropy alloys with different additions of TiO2 nano-ceramic particles (0, 1.25vol.%, 2.5vol.%, 3.75vol.% and 5vol.%, respectively) were prepared by using the vacuum arc melting method. The effects of TiO2 addition on the crystal structure, microstructures and mechanical properties of the alloy were investigated by X-ray diffraction (XRD), scanning electron microscopy (SEM), transmission electron microscopy (TEM), and tensile testing. The microstructure analysis shows that the TiO2 nano-ceramic particles added in the alloy are decomposed, and a small amount of Al2O3 and a great number of intermetallic compounds (γ′ phases) with simple cube structure are formed. The γ′ phases are enriched at inter-dendrite, which increases the resistance of dislocation movement during the deformation of the alloy, thus balancing the problem of high plasticity and low strength of the alloy. When the addition of TiO2 is 2.5vol.%, the strength of the high-entropy alloy reaches the maximum of 489 MPa, which is 11.1% higher than the matrix alloy composed of single FCC phase.

Interface characteristics and mechanical properties of Al0.6CoCrFeNi/5052Al matrix composites fabricated via vacuum hot-pressing sintering and annealing

In this study, Al0.6CoCrFeNi high-entropy alloy particle reinforced 5052Al matrix composites prepared via vacuum hot-pressing sintering were annealed. Experimental techniques such as SEM, XRD, EPMA, Vickers hardness, and uniaxial compression were used to characterize the prepared composites' microscopic morphology and mechanical properties. Furthermore, the Boltzmann-Matano diffusion theory and diffusion layer thickness curve fitting methods were used to predict the trend of the thickness of the diffusion layer under various annealing conditions. The results of this study suggest that the thickness of the diffusion layer increased parabolically with an increase in annealing temperature or annealing time. The intermetallic compounds (IMCs) generated in the diffusion layer region were Al13Co4-, Al9Co2-, and Al18Cr2Mg3-type phases. The mechanical properties of the composites were closely related to the change in the thickness of the diffusion layer: when the annealing temperature was 773 K/8 h, the compressive strength and microhardness of the composites reached the maximum values of 345.7 MPa and 82.8 HV0.2, respectively. Furthermore, the linear fitting method with the addition of the incubation period provided the best fit to the experimental values and provided a reference for subsequent modulation of the composite properties by varying the thickness of the diffusion layer.

Effect of Heat Dissipation Rate on Microstructure and Mechanical Properties of Al0.5FeCoCrNi High-Entropy Alloy Wall Fabricated by Laser Melting Deposition

High-entropy alloys (HEAs) are a new type of multi-component alloy. The design of the compositions breaks the design ideas of traditional alloys and shows many excellent properties. Therefore, an Al0.5FeCoCrNi HEA with face-centered cubic (FCC) and body-centered cubic (BCC) dual-phase structure was used in this paper. During the additive manufacturing process, the heat dissipation rate gradually changes with the increase in wall height. As a result, the composition of the phases changes, resulting in differences in mechanical properties. Here, we designed laser melting deposition (LMD) on T-beams of different heights to change the heat dissipation rate of the wall, and the effects of the heat dissipation rate on the microstructure and mechanical properties of Al0.5FeCoCrNi HEAs were studied. The experimental results showed that increasing the height of the T-beam would gradually slow down the heat dissipation rate of the wall. The above phenomena not only led to a gradual reduction of the BCC phase under the influence of heat accumulation but also increased the length of columnar crystals in the wall with the slowing of heat dissipation. Heat accumulation hindered the nucleation during solidification and eventually led to the growth of grains across the deposition layer. Furthermore, the slow heat dissipation rate changed the grain number and BCC phase content, which gradually decreased the strength and hardness, while the ductility of the samples improved.