The China fusion engineering test reactor is a bridge between the international thermonuclear experimental reactor and future fusion demonstration reactors. The harsh service environment of the fusion reactor, including high heat flow density, strong neutron irradiation, and high temperature and high pressure coolant corrosion, demands higher requirements on structural materials than conventional nuclear energy structural materials. Low activation oxide dispersion-strengthened (ODS) steels, which are developed based on reduced activation ferritic/martensitic steels, are considered as promising candidate fusion reactor structural materials because of their high creep strength and excellent resistance to irradiation. In this study, 9Cr-ODS steel prepared by mechanical alloying (MA) and Chinese low activated martensitic (CLAM) steel prepared by vacuum smelting were selected because of their excellent mechanical properties and superior radiation tolerance. The main difference between the two steels is the grain size: the average grain size of the 9Cr-ODS steel is 200-500 nm, whereas that of CLAM steel is 10-20 μm. Furthermore, the 9Cr-ODS steel was added with Y₂O₃ during MA, which improved its mechanical properties and thermal stability. Corrosion experiments were conducted in static and dynamic (flow rate of 5 mL/min) ultrapure water at 325 ^oC and 15.5 MPa. Ultrapure water had an electrical conductivity of 0.1 μS/cm and a dissolved oxygen content of 10 × 10^-9. The exposure time for both steels were set as 200, 500, and 1000 h. Results indicated that under static and dynamic conditions, the corrosion mass gain and oxide film thickness of the 9Cr-ODS steel were less than those of the CLAM steel. Under static conditions, the corrosion product of both materials exhibits a double-layer structure with granular Fe₃O₄ in the outer layer and continuous Cr- and Fe-rich spinel in the inner layer. As the exposure time increased from 200 h to 1000 h, the size and thickness of the oxide particles gradually increased. However, under dynamic conditions with a flow rate of 5 mL/min, the surface of the 9Cr-ODS steel formed not only Fe₃O₄ but also a small amount of Fe₂O₃, while the type of oxide in the outer layer of the CLAM steel remains unchanged. In contrast to the static condition, both steels exhibited decreased corrosion mass loss and oxide film thickness because of the dynamic water scouring effect and the buildup of H₂ on the surface caused by water decomposition through oxidation. Overall, under same corrosion conditions, the presence of dispersed oxides, grain refinement, and a high matrix oxygen concentration positively enhanced the corrosion resistance of the 9Cr-ODS steel. This enhancement facilitated the formation of a protective inner oxide layer and reduced the corrosion mass loss rate, thereby demonstrating the superior corrosion resistance of the 9Cr-ODS steel under high temperature and high pressure water environments compared with the CLAM steel.

Lead-cooled fast reactor (LFR) is one of the most promising reactor types among the six reactor concepts outlined in the Technology Roadmap for Generation IV Nuclear Energy Systems. Lead-bismuth eutectics (LBEs) are often used as coolants for LFRs because of their excellent economy and safety. However, structural materials are eroded by high-density LBEs at high temperatures. The compatibility between LBE and structural materials is a key problem that must be urgently solved for the development and application of LFRs. Due to the pinning of dislocations and grain boundaries as well as capture of displaced atoms and helium bubbles by oxide nanoparticles, oxide dispersion strengthened (ODS) alloys exhibit outstanding high-temperature mechanical properties and swelling resistance under irradiation. Fe-based ODS alloys have emerged as candidates for cladding tubes and structural materials in advanced reactors. A protective alumina scale can be formed on the alloy surface by adding Al to ODS alloys, which prevents the further penetration of LBEs into the alloy substrate. However, Y-Al-O complex-oxide nanoparticles with a slightly larger size compared to Y-Ti-O complex nanoparticles (in ODS FeCr alloy) are also formed in the alloy, leading to a slight decrease in the high-temperature strength of ODS FeCrAl alloys. It is known that adding a small amount of Zr to ODS FeCrAl alloys is an effective strategy to compensate for the decrease of mechanical properties caused by the coarseness of oxide nanoparticles, as numerous small-sized Y-Zr-O complex nanoparticles would preferentially precipitate instead of Y-Al-O complex nanoparticles. Thus far, studies on the corrosion behavior and corresponding mechanism of ODS FeCrAl alloys containing Zr in LBEs have been scarce. In this work, ODS FeCrAl alloys containing Zr were prepared via powder metallurgy. After the alloys were corroded by an oxygen-saturated static liquid LBE at 550 ^oC for 10000 h, its corrosion products were characterized by SEM, XRD, and EPMA. The effects of Zr, Ti, Al, and O contents on the corrosion resistance of ODS FeCrAl alloys were studied. Due to the combination of Zr and O and its interference with the outward diffusion of Al at the initial stage of oxidation, no continuous, protective aluminum oxide scale was formed on the surface of the ODS FeCrAl alloys. The corrosion products were mainly composed of thin alumina scale and multilayer oxide nodules, and no peeling of oxidation products was observed on any of the specimens. Further, it was revealed that the outer layer of these oxide nodules was composed of Fe₃O₄ with a magnetite phase, the inner layer was composed of spinel FeCr₂O₄ and Fe(Cr, Al)₂O₄, and the internal oxidation zone (IOZ) contained the oxide of Al and Cr. In addition, the distribution and morphology of oxide nodules were also affected by the contents of Ti, Al, and O in the alloys. With an increase in O content, high-density Y-Zr-O complex nanoparticles precipitated in the ODS FeCrAl alloys containing Zr, which led to a reduction in the content of residual Zr in the substrate. Consequently, the Zr content, which adversely affected the formation of alumina scale, was reduced, and the quantity, thickness, and surface transverse dimension of oxide nodules decreased. Introducing Ti into the ODS FeCrAl alloys containing Zr was also found to be unfavorable to the formation of the alumina scale as its impact on corrosion behavior was similar to that of Zr. With the addition of Ti, an increased number of oxide nodules were formed on the surface of Zr-containing ODS FeCrAl alloys. Because the addition of (4.0%-5.5%)Al does not prevent the formation of Fe-rich oxide nodules on the ODS FeCrAl alloys containing approximately 0.3%Zr, it is necessary to further increase the Al content in the matrix to obtain a continuous alumina scale.

This research introduces a coupled dynamic model, which involves refining slag, molten steel, inclusions, and refractory materials, to explore the modification effects of CaO-MgO-Al₂O₃ refining slag on Al₂O₃ inclusions within steel. The study examines the impact of varying aluminum contents in steel and CaO / Al₂O₃ ratios in slag on inclusion modification. Notably, the Ca content in both steel and inclusions exhibits a positive correlation with the Al content in steel and the CaO / Al₂O₃ ratio in the slag. An increase in the Al content in steel from 0.01% to 0.75% led to a rise in the Ca content in the molten steel from 0.07 × 10^-6 to 1.47 × 10^-6, accompanied by an increase in the CaO content in inclusions from 0.44% to 7.89%. Additionally, elevating the CaO / Al₂O₃ ratio in the slag from 1.0 to 2.2 enhanced the Ca content in the molten steel from 0.15 × 10^-6 to 0.50 × 10^-6 and increased the CaO content in inclusions from 0.88% to 2.95%. When the Al content in the steel reached 0.8% and the CaO / Al₂O₃ ratio in the slag stood at 2.2, the total Ca content in the steel escalated to 2.52 × 10^-6, while the CaO content in inclusions surged to 10.96%. These results affirm that CaO-MgO-Al₂O₃ refining slag is capable of effectively transforming Al₂O₃ inclusions into CaO-Al₂O₃ inclusions, with the modification extent predominantly influenced by the Al content in the steel.

Improving the hardenability of a ferrous alloy to achieve uniform microstructures and mechanical properties along the direction of the plate thickness is a key challenge in the production of high-grade extra-thick steel plates suitable for marine engineering (hereinafter referred to as “marine steel”). Hence, in this study, the effect of V distribution on the microstructures and hardenability of marine steel was investigated by employing the following procedure: a novel 980 MPa grade extra-thick steel plate was subjected to austenitization at 850 and 910 ^oC; subsequently, through thermal expansion and Jominy end-quench tests combined with fixed nitrogen treatment with aluminum. The microstructures and state of V atoms in the marine steel sample were characterized using SEM, EPMA, and TEM. Results showed that the occurrence of AlN during austenitizing at 910 ^oC promoted the segregation of V atoms on the original austenite grain boundaries, improved the stability of undercooled austenite, and delayed the transformation of proeutectoid ferrite. Thus, this study showed that the incorporation of V in marine steel substantially improved the hardenability of marine steel over a wide range of cooling rates (corresponding to steel plates with thicker cross-sections) and facilitated better microstructure uniformity, performance in marine environments, and matching between the required strength and toughness.

Recently, 2 GPa grade ultra-high strength steel has emerged as a potential candidate material for torsional axles. Nevertheless, studies focusing on the correlation between the microstructure and mechanical properties are scarce. To address this, the current study investigates the impact of austenitizing temperature on the microstructure, tensile mechanical properties, and static torsional properties of 2 GPa grade ultra-high strength steel used in torsion axles. Various techniques including SEM, EBSD, AES, TEM, uniaxial tension, and static torsion are employed. During the austenitizing process, the lamellar cementite in the initial microstructure (composed of pearlite and a minimal amount of ferrite) first spheroidized and then dissolved. This spheroidization process is primarily dominated by discontinuity-assisted spheroidization, with minimal contributions from termination-migration-assisted spheroidization. With increasing austenitizing temperature, the cementite gradually transforms from (Fe, Cr, V)₃C to Fe₃C, eventually completely dissolving (at the austenitizing temperature of 950 ^oC). Moreover, the precipitation temperature range of vanadium carbide is consistent with the temperature range of undissolved cementite. Additionally, austenitizing at 850 ^oC and tempering at 220 ^oC results in better tensile properties, including a yield strength of 1580 MPa, tensile strength of 2062 MPa, uniform elongation of 8.4%, and total elongation of approximately 12.7%. These improvements are attributed to the precipitation strengthening enabled by cementite and vanadium carbide and the fine grain strengthening provided by fine martensite block sizes. The static torsion test results show that when the austenitizing temperature is 800 and 850 ^oC, the sample shows the best shear moduli and torsional yield strength due to the increased cementite and vanadium carbide contents, along with fine martensite block sizes. With increasing austenitizing temperature, the shear plastic deformation zone expands, and the predominant fracture mechanism changes from shear fracture to shear ductile fracture, resulting in higher torsional strengths.

The turbine disk is a crucial heat-resistant component of aeronautical engines. An investigation into the similarities and differences in the microstructure and mechanical properties of superalloys fabricated using powder metallurgy and conventional casting and wrought methods could provide a theoretical framework for ensuring the production and operational reliability of turbine disks that are difficult to deform. GH4720Li (Udimet720Li) alloy is a commonly used nickel-based superalloy reinforced through precipitation. The volume fraction of γ' precipitation in GH4720Li alloy is 45%. It is mainly used to make compressor and turbine disks for use at 650-750 ^oC, as well as turbine disks for use at 900 ^oC in a short time. The mechanical properties of the GH4720Li alloy are closely associated with its microstructure. The mechanical properties of the alloy, including hardness, yield strength, and tensile strength, are influenced by factors such as grain size and orientation, distribution of the γ′ phase, presence of twins, and arrangement of grain boundaries. To investigate the similarities and differences of the microstructure and mechanical properties between powder alloy (FGH4720Li alloy) and wrought alloy (GH4720Li alloy), which were prepared by powder metallurgy and traditional cast and wrought processes, the microstructure characteristics of FGH4720Li alloy and GH4720Li alloy were observed and analyzed by SEM, TEM, and EBSD (FGH4720Li alloy). The mechanical properties of both alloys were studied via Vickers hardness and high-temperature tensile tests. Furthermore, the relationship between the microstructure and mechanical properties of both alloys was thoroughly discussed. Results show that the distribution characteristics of dislocation, twin substructure morphology, grain orientation concentration, and twin boundary in both alloys are similar. Wide twins (0.5-1 μm) and some narrow twins (< 100 nm) were observed in both two alloys, and the type of twin boundary is primarily Σ3. No obvious preferred orientation was noticed in both alloys. The difference is that the size of γ{}_{\mathrm{I}}^{\text{'}} phase in the GH4720Li alloy (1.92-2.41 μm) is larger than that in the FGH4720Li alloy (1.41-1.51 μm), whereas the size of γ{}_{\mathrm{I}\mathrm{I}}^{\text{'}}phase in the powder FGH4720Li alloy (66.24-73.15 nm) is higher than that in the GH4720Li alloy (64.74-72.29 nm); additionally, a petal-like γ{}_{\mathrm{I}\mathrm{I}}^{\text{'}} was observed in the FGH4720Li alloy. The proportion of grain size between 12 and 24 μm in the GH4720Li alloy is higher than that in the FGH4720Li alloy, and the microstructure of the GH4720Li alloy contains some coarse grains (32-36 μm). The percentage of high angle grain boundaries in both alloys is higher than 83%. However, FGH4720Li alloy has a higher fraction of low angle grain boundaries than GH4720Li alloy. Additionally, FGH4720Li alloy exhibits a more pronounced variation in intracrystalline orientation. Furthermore, FGH4720Li alloy with small average grain size exhibits higher hardness, yield strength, and ultimate tensile strength than GH4720Li alloy.

GH3230 superalloy has excellent high-temperature mechanical properties and oxidation resistance; hence, it is widely used to manufacture key high-temperature structural components in the aerospace and other fields. In the research, development and production process of aero-engines and gas turbines, GH3230 superalloy plate is often used to make the welded components of a combustion chamber. Excellent weldability is an important technical index and is also an important basis for the plate component design and welding process formulation. For GH3230 superalloy welded plates used at high temperature, the stability of the microstructure of the welded joint is closely related to the mechanical properties of welded components. However, in theory, some deficits remain in the in-depth study of scientific problems regarding GH3230 superalloy welding; hence, the microstructure evolution of welded joint during its long-term service at high temperature has attracted attention. This study focuses on observing and analyzing the experimental phenomena of microstructural changes in welded joint (in the weld and heat affected zones), changes in the alloy element content of carbides, the coarsening rate of carbides, and degradation reaction between carbides after long-term thermal exposure at various high temperatures. Experimental results show that in the tungsten argon-arc welded thin plate of GH3230 superalloy, the dendrite morphology of the weld zone disappears after 2000 h of thermal exposure. Furthermore, the degree of dendrite segregation decreases remarkably, grain size in the heat affected zone becomes uneven, and carbide precipitation in the grain and grain boundary increases obviously. After long-term thermal exposure at various temperatures, the solid solubility and content of alloying elements in two types of carbides—(Cr, W)₂₃C₆ and (W, Cr)₆C—in the welded joint change and coarsening rate of M₂₃C₆ carbide exhibits an obvious increase. During the long-term thermal exposure of the argon-arc welded thin plate, the microstructures of the weld and heat affected zones undergo alloy carbide degradation based on diffusion, which changes the type, quantity, size, morphology, and location distribution of carbide.

Three-dimensional fabric-reinforced aluminum matrix composites with high specific strength and modulus, excellent high-temperature resistance, and impact resistance are ideal structural materials for fabricating heat-resistant components in aeronautics and aerospace engineering. However, few studies have explored the mechanical properties and fracture behaviors of these composites in high-temperature environments. This study aims to investigate the quasi-static tensile behaviors and failure mechanisms of a stitched twill carbon fabric-reinforced aluminum matrix composite at an elevated temperature of 400 ^oC. Based on the fabric structure and yarn microstructure, a mesoscle finite element model was established using representative unit cells at the microsale and mesoscale. The macroscopic mechanical response, damage evolution, and failure mechanism of the composite during the tensile test at an elevated temperature (400 ^oC) were analyzed through numerical simulations and experiments. Results show that the tested tensile modulus, strength, and fracture strain at 400 ^oC are 103.20 GPa, 621.60 MPa, and 0.819%, respectively. The calculated tensile stress-strain curve aligns with the experimental curves obtained from high-temperature tensile tests. The composites experience complex thermal stress at elevated temperatures, with the matrix pocket under compressive stress and the yarn structure under tensile stress. In the initial tensile stage, the matrix between interlaced weft/warp yarns is damaged, and local failure zones appear in the stitch and warp yarns; however, the composite exhibits a linear elastic response. As the tensile load increases, the degree of damage in the matrix pocket gradually increases, leading to the emergence of serious matrix damage zones and weft yarn cracking along the twill direction of the fabric. Consequently, the growth rate of tensile stress in the tensile curve declines with increasing tensile strain. In the final stage, the matrix failure zone and yarn fracture zone overlap. The axial fracture of warp yarn, in particular, leads to catastrophic fracture of the composite, resulting in a dramatic drop of the tensile stress. The stitch and weft yarns in the composites exhibit a flat fracture morphology, whereas the fractured warp yarn presents rugged fracture surfaces. A mass of fiber pull-out is observed on the microscopic fracture surface of a warp yarn, accompanied by matrix alloy tearing characteristics.

With increasing power of aero-engines, the effects of temperature and load on hot-end parts such as bearings and bushings are becoming more apparent, leading to the wear failure of hot-end parts. Therefore, increasing the wear resistance of hot-end parts is very important. Laser-clad coatings can considerably improve the mechanical properties and wear resistance of these parts, without altering the properties of the substrate. The use of such coatings provides a new approach to improve the high-temperature wear resistance of hot-end parts. Mo alloys with high melting point, excellent high-temperature strength, and low thermal expansion coefficient have been widely used as high-temperature materials. Therefore, these coatings fabricated using the laser cladding technology have good prospects for application as wear-resistant coatings on the surface of hot-end parts at elevated temperatures. To further enhance the wear resistance of the Mo alloy coatings for application as high-temperature protective coatings for hot-end parts, MoNiCrSi coatings were in situ prepared on the surface of the Inconel 718 alloy via laser cladding. The effects of Si on the microstructure and high-temperature tribological performance of the Mo alloy coatings were systematically studied. The high-temperature wear tests of the Mo alloy coatings and Inconel 718 alloy were performed using a ball-on-disk tribo-tester against Si₃N₄ balls in an environment where the temperature varied from room temperature to 1000 ^oC. The results indicate that Si reacts with Mo, Ni, and Cr to form α-Mo, Mo_0.3Ni_0.24Si_0.76, Mo₅Si₃, and CrSi₂ phases. Compared with the MoNiCr coating and substrate, the MoNiCrSi coating has higher microhardness. The introduction of Si causes solid solution strengthening and dispersion strengthening effects. The friction coefficients of coatings gradually decrease with increasing temperature. The wear rates firstly decrease and then increase with increasing temperature. Furthermore, with an increase in the temperature, the substrate material exhibits the highest wear rates, reaching a maximum value of 3.41 × 10^-4 mm³/(N·m) at room temperature (24 ^oC). However, the high-temperature wear resistance of the MoNiCrSi coating is the best than that of the MoNiCr coating or substrate, and the wear rates of the MoNiCrSi coating are in the order of magnitude of 10^-6-10^-5 mm³/(N·m) in the temperature range from room temperature to 1000 ^oC. This finding indicates that the introduction of Si drastically improves the high-temperature wear resistance and self-lubricating properties of the Mo alloy coating at elevated temperatures. This improvement is primarily attributed to the synergistic effects of the high hardness of the coatings and introduction of solid lubricants, such as SiO₂, MoO₃, Mo₄O₁₁, and NiMoO₄, as well as an oxide lubricating layer on wear tracks. In particular, at 600 ^oC, the MoNiCrSi alloy coating has the lowest wear rate of 5.57 × 10^-6 mm³/(N·m), which is one order of magnitude lower than that of the MoNiCr coating. The Mo alloy coatings exhibit various wear mechanisms at different temperatures. At room temperature, the main wear mechanisms are fatigue wear, abrasive wear and plastic deformation. At 600 ^oC, the oxidation wear, fatigue wear, and abrasive wear become the primary wear mechanisms. At 1000 ^oC, the dominant wear mechanism of the coatings is oxidative wear.

CrAlN coatings have garnered significant attention in the fields of cutting tools and plastic injection molds because of their high hardness, excellent thermal stability, and superior oxidation resistance. However, their applicability under the harsh conditions of aluminum alloy die casting and hot stamping dies is curtailed by the coatings' high coefficient of friction and limited impact toughness. By adopting a multiple alloying and high-throughput approach, this study focuses on the fabrication of CrAlMoN solid solution coatings with varying Mo contents on H13 steel substrates using arc ion plating technology. The effects of Mo content on the microstructure, mechanical and tribological properties of the coatings were thoroughly examined. Characterization techniques such as XRD, SEM, and EDS were employed to analyze the phase structures, surface cross-sectional morphology, and elemental distribution of the coatings. Mechanical properties, including hardness, film-base adhesion, and toughness, were assessed using a CMS scratch tester and a nanoindentation tester. The friction properties were evaluated using a tribometer in an atmospheric environment. The findings indicate that increasing the Mo content (atomic fraction) from 0.72% to 19.47% resulted in the incorporation of Mo atoms into the (Cr, Al)N lattice, forming a typical solid solution coating with a minor presence of Mo₂N crystal phases. Notably, at a Mo content of approximately 2.55%, the coatings achieved peak hardness (38.7 ± 1.3) GPa and elastic modulus (580.9 ± 11.1) GPa, along with enhanced toughness due to improved crack resistance. Tribological experiments demonstrated remarkable wear resistance at 25 ^oC, with a coefficient of friction (COF) ranging from 0.32 to 0.51 and wear rates of (5.90-10.88) × 10^-7 mm³/(N·m). The low COF and wear rates are attributed to the formation of Magnéli-phase oxide MoO₃, which facilitates low shear during friction. A further increase in the Mo content to 19.47% led to even better tribological properties, as indicated by the lowest observed COF of 0.31 and a wear rate of 5.90 × 10^-7 mm³/(N·m). The microstructural analysis revealed that the accumulation of MoO₃ phases during friction contributed to the coatings' tribological performance, with wear primarily resulting from the combined effects of abrasive wear and severe oxidation, accompanied by minor pitting delamination from the substrates.

It is crucial to accurately predict and control the overall microstructure uniformity of large forgings to enhance their comprehensive mechanical properties. Common empirical models of dynamic recrystallization (DRX) do not consider the nucleation mechanisms and grain boundary migration driven by stored energy differences, thereby limiting their ability to predict and track nucleation events and microstructure morphology during the DRX process. To address this limitation, this study proposes an effective simulation approach for microstructure morphology evolution by integrating the level-set method with a dislocation model. The level set function, implemented on a fixed grid within the Eulerian framework, enables the numerical tracking of evolving curves or surfaces on Cartesian grids. Further, it also facilitates topological evolution handling, thereby eliminating the need for complex curve or surface parameterization. Parameters of the DRX model based on the level set method were determined using stress-strain experimental data of the GH4706 alloy within the temperature range of 950-1150 ^oC and strain rate range of 0.001-1 s^-1. Although certain model parameters were obtained through fitting, the two critical parameters of nucleation volume per unit time at the grain boundary surface and factor affecting grain boundary migration rate could not be determined in this way. These were instead identified using a Pareto multi-objective optimization method, which iteratively minimized the discrepancy between experimental data and simulated results through reverse analysis. The DRX fraction and the average grain size were selected as the optimization objectives. The average deviation percentages between the experimental data and simulated results of the two optimization objectives under varying strain conditions were used as evaluation functions. Through continuous multi-objective iterative optimization, an optimal parameter set was derived. Simulation results for the GH4706 alloy under different parameter combinations revealed a linear relationship between the DRX model parameters with the process variables. The DRX behavior of the GH4706 alloy under strains of 0.4-0.7 was simulated and experimentally validated. A comparison between the experimental data and simulation results showed that the average deviation of both the DRX grain volume fraction fraction and grain size was less than 10%. This confirmed the validity of the model and parameter identification approach. Thus, this study provides a robust theoretical framework for simulating the microstructure uniformity of GH4706 alloy during large forgings and offers valuable insights for predicting and regulating the microstructural uniformity.

Additively manufactured (AM) Ti-6Al-4V alloys are known for their lightweight and superior mechanical properties and are increasingly being favored in the aerospace, energy, and biomedical industries. Among the available AM technologies, selective laser melting (SLM) stands out for its ability to fabricate complex-shaped Ti-6Al-4V efficiently and economically through near-net-shape manufacturing. Despite their advantages, SLM-produced parts often suffer from mechanical anisotropy and contain microdefects such as pores, cracks, and residual stresses, restricting their wider application. Addressing these issues requires a thorough understanding of the effects of texture and porosity on the mechanical properties of AM materials, which is necessary for developing components that comply with strict industry standards. Previous research has predominantly focused on studying the impact of texture or porosity on material properties, overlooking the interplay between these two critical factors. This work introduces an advanced modified Mori-Tanaka (MMT) model that simultaneously considers both texture and porosity in dual-phase AM Ti-6Al-4V alloys. This model enhances the traditional Mori-Tanaka approach by integrating it with the differential method, facilitating a nuanced analysis of how texture and porosity jointly influence the mechanical behavior of polycrystals. For model development, phase transitions and grain orientations are characterized using EBSD, whereas the 3D Gaussian distribution function describes the texture distribution within the polycrystal. Micro/nano computed tomography (CT) plays a pivotal role in determining the volume fraction and morphology of pores, providing crucial data for the model. These parameters were incorporated into the mesomechanical model to analyze the effective elastic stiffness tensor and Young's modulus, quantifying their collective impact on the alloy's mechanical properties. To validate the model, tensile and ultrasonic tests are conducted for two samples with different porosities and textures and compared their outcomes to evaluate the material's mechanical behavior, which exhibits characteristics of transverse isotropy. The comparison highlights the MMT model's superior precision, especially at higher porosity levels, with mean absolute percentage errors (MAPE) between Young's modulus obtained from the MMT model and the tensile test for two samples were 0.87% and 2.51%, respectively. Similarly, the MAPE between the effective elastic stiffness tensor derived from the MMT model and the ultrasonic test were 9.47% and 4.45%, respectively. These findings underscore the model's effectiveness in predicting material properties and its potential as a robust tool for exploring the interactions between microstructural elements and macroscopic mechanical properties of AM polycrystalline materials.