Low Stacking Fault Energy Research Articles

Microstructural Investigations of Weld Deposits from Manganese Austenitic Alloy on X2CrNiMoN22-5-3 Duplex Stainless Steel

Duplex stainless steels are materials with high performance under mechanical stress and stress corrosion in chloride ion environments. Despite being used in many new applications such as components for offshore drilling platforms as well as in the chemical and petrochemical industry, the automotive industry, etc., they face issues of wear and hardness that limit current applications and prevent the creation of new use opportunities. To address these shortcomings, it is proposed to develop a hardfacing process by a special welding technique using a universal TIG source adapted for manual welding with a pulsed current, and a manganese austenitic alloy electrode as filler material. The opportunity to deposit layers of manganese austenitic steel through welding creates advantages related to the possibility of achieving high mechanical characteristics of this steel exclusively in the working area of the part, while the substrate material will not undergo significant changes in chemical composition. As a result of the high strain hardening rate, assisted mainly by mechanical twinning, manganese austenitic alloys having a face-centered cubic crystal lattice (f.c.c) and low stacking fault energy (SFE = 20–40 mJ/m2) at room temperature, exhibit high wear resistance and exceptional toughness. Following cold deformation, the hardness of the deposited metal increases to 465 HV5–490 HV5. The microstructural characteristics were investigated through optical microscopy (OM), scanning electron microscopy (SEM), energy-dispersive X-ray analysis (EDX), X-ray diffraction (XRD), and Vickers hardness measurements (HV). The obtained results highlighted the feasibility of forming hard coatings on duplex stainless steel substrates.

Temperature/stress dependence of stress rupture behavior and deformation microstructure of an advanced superalloy for additive manufacturing

A self-developed crack-free advanced superalloy ZGH451 fabricated by direct energy deposition (DED) was applied to investigate the microstructure evolution, stress rupture behavior, and deformation mechanisms at moderate-high temperatures and high-low stress conditions. The high Ta/Al ratio induces large misfit lattice stress and low stacking fault energy of alloy, resulting in approximate cubic γ′ phases in dendrites and the formation of initial dislocation tangles. After the stress rupture test at 760 °C/780 MPa, high content cubic γ′ phases, small size of voids as well as preserved dislocation tangles are observed, showing stable structures with high-stress rupture resistance. High content and suitable size of cubic γ′ phases, initial dislocation tangles, and L-C locks hinder the dislocation motion, which decreases the minimum strain rate and prolongs life significantly, forming four stress rupture stages. Hence, the deformation mechanism is determined by dislocation piled-up on γ/γ′ interface, formation of stacking faults in γ′ phases, and dislocations shearing γ′ phases. However, the microstructure exhibits uneven structures composed of large sizes of rafted γ′ phases and voids at 980 °C/260 MPa. The rafted structure and high temperature provide continuous channels and enough energy for dislocation motion, resulting in the increase of minimum strain rate, decline of life, and typic three stress rupture stages, even though there are obstacles to dislocation movement caused by dislocation networks. The deformation mechanism transforms to form dislocation networks on γ/γ′ interface and dislocations shearing γ′ phases. Besides, the decomposition of carbides on GBs also depends on temperature, which decomposes into harmful chain-like M23C6 carbides at moderate temperatures and reinforced granular-shaped M6C carbides at high temperatures. The applied stress always decreases mechanical properties due to its degradation of microstructure induced by elongating the precipitates and defects.

Achieving high ductility at medium temperature in a nonequiatomic CoCrNi alloy

The tensile strength and ductility of face-centered cubic (FCC) multi-principal element alloys (MPEAs) typically decline monotonically with increasing temperature. In this work, we conducted tensile tests at different temperatures and characterized deformation microstructures for a nonequiatomic CoCrNi alloy with low stacking fault energy (SFE). Exceptional ductility is obtained at medium temperature, breaking the general sense of monotonic change with temperature. The effect of deformation mechanisms of dislocations, stacking faults and phase transformation on the ductility was discussed. This work reveals the unique temperature effect on the mechanical properties of metals with very low SFE.

Effect of abnormal grain refinement on synchronous strengthening behavior of Fe50Mn30Co10Cr10 high entropy alloys

Improving processing efficiency while obtaining excellent material formation and mechanical properties is the primary concern of the manufacturing industry. This study aims to refine the grains of Fe50Mn30Co10Cr10 high entropy alloy during friction stir processing, achieving exceptional tensile properties in the stir zone by increasing the rotational speed. The key driver behind grain refinement lies in the alloy's inherently low stacking fault energy, with the primary recrystallization mechanism being discontinuous dynamic recrystallization. The freshly recrystallized fine grains share analogous microstructures and energy levels during severe plastic deformation, which engenders a state of increased competition among them. This robust competitive dynamic impedes grain growth, thereby promoting the development of refined grains. This microstructure proves instrumental in avoiding premature microcracking during tensile loading by hindering martensite formation, consequently improving the UTS and EL of the material. Nevertheless, the high heat input and substantial strain result in an increase of temperature and strain energy in the system, eventually disrupting the high energy system and causing grain coarsening as the rotational speed continues to increase. This coarsened grain and high martensite fraction lead to premature initiation of cracks under tensile loading, which is not conducive to further improvement of tensile properties.

Achieving ultra-strong and ductile CoNi-based FCC multi-principal element alloys via alloying with refractory Mo and W

FCC single-phase multi-principal element alloys (MPEAs) often suffer from insufficient strength, which limits their wide applications. Here a CoNi-based FCC MPEA (Co44Ni44Mo9W3, at. %) was designed by alloying with refractory Mo and W. The Co44Ni44Mo9W3 alloy possesses an ultrahigh yield strength of ∼1050 MPa and good ductility of ∼30 % at ambient temperature. The excellent mechanical properties were correlated to its superior lattice friction stress and grain boundary strengthening compared to most reported FCC MPEAs and conventional alloys. By density-functional theory calculations, such extraordinary mechanical properties were further attributed to its high lattice distortion, low intrinsic stacking fault energy and high unstable stacking fault energy due to the addition of Mo and W. Transmission electron microscopy investigations revealed that the high strength-ductility combination arises from the synergistic effect of planar slip bands, stacking faults and deformation nano-twins.

Effect of cooling rate and Nb addition on the strengthening in eutectic CoCr1.3FeMnNi0.7Nbx (0 ≤ x ≤ 0.45) high entropy alloys comprising of low stacking fault energy FCC phase

The CoCr1.3FeNi0.7MnNbx (0.3 ≤ x ≤ 0.45) eutectic high entropy alloy (EHEA) comprising of ultrafine lamellae of low stacking fault energy (SFE = 11 mJ/m2) face centered cubic (FCC) and Laves phase are synthesized at cooling rates of 2.5–10 K/s (arc melted ingots, AMIs) and 4.2 × 102 K/s (suction cast bars, SCBs). The microstructural investigation suggests that secondary dendritic arm spacing (SDAS) and interlamellar spacing are refined in SCBs due to a higher cooling rate than the AMIs. Whereas, deformation twins evolve in FCC phase due to its low SFE. The EHEAs exhibit a high yield strength of 1327 MPa for x = 0.367 SCB and a large fracture strain of 20% for x = 0.3 AMI under compression. Systematic investigation on the influence of Nb addition, microstructure refinement, and evolution of deformation twins during straining on the strengthening mechanisms reveals that the phase interface strengthening, solid solution strengthening, and twin boundary strengthening play critical roles in providing the high flow stress. The post-deformation analysis and the presence of multiple positive slopes in work hardening curves confirms that the concurrent effect of the evolution of dislocations, deformation twins, and their mutual interactions are solely responsible for the severe strain hardening at multiple stages during plastic deformation. The low values of strain rate sensitivity (0.0106–0.0111) and the activation volume (28b3-41b3) suggest that the deformation kinetics is governed by the dislocation interactions with the ultrafine lamellae interface and twin boundaries.

Favourable conditions for strain induced transformations in unstable high-manganese steel

The present research is part of a project that includes several grades of high‑manganese steels with different chemical compositions and various pre-treatment parameters. The main objective of this work was to determine favourable conditions for the occurrence of strain-induced phase transitions in unstable Fe-20Mn-3Al-3Si steel. After preliminary treatment the steel showed a two-phase microstructure consisting of austenite matrix and 29% of ferrite volume fraction. The deformation process of the examined steel was strongly influenced by the low stacking fault energy value of austenite matrix. Initially, the slip of dissociated dislocations led to the formation of numerous bands of stacking faults. Then, the phase transformations induced by plastic deformation took place, i.e., γ (fcc) → ε (hcp) and subsequently ε (hcp) → α’ (bcc). The beginning and further progress of these phase transitions depended primarily on the crystallographic orientations of the austenite grains. The more favourable the orientation of the grains with respect to external stresses, the more effective was the activation of dislocation slip and the greater number of deformation bands was formed. These processes directly resulted in a locally induced phase transition γ → ε. Simultaneously, in grains showing the formation of ε-bands in at least two intersecting systems, the transformation ε → α’ gradually occurred.

Effect of Ga on the microstructure and properties of NiCoV alloy at different annealing temperatures

To obtain a high-entropy alloy characterized by high strength and plasticity, (NiCoV)100-xGax (x ​= ​0, 5, 7) was successfully prepared, cold-rolled, and heat-treated. The microstructure was analyzed to correlate Ga content with the performance of the system. The addition of Ga can produce alloying effects, including solid solution strengthening effect, second phase precipitation strengthening effect, and layer misalignment energy reduction effect. The experimental results show adding Ga elements can enrich Ni, Co, V, and Ga above the grain boundaries, causing the alloy to produce annealed twins inside. The alloy is strengthened mainly by precipitation, and the formation of the precipitation phase effectively enhances the strength of the alloy. The low stacking fault energy promotes the toughening of NiCoV but makes the plasticity of the alloy decrease. Still, the formation of annealed twins effectively increases the plasticity, which makes the alloy harder but does not reduce the plasticity too much. By comparing the experimental properties, (NiCoV)93Ga7 showed the best mechanical properties at the annealing temperature of 900 ​°C, yield strength, tensile strength and elongation of 906 ​MPa, 1321 ​MPa and 21.36 ​%, respectively.

Improving the hot corrosion resistance of additively manufactured Inconel 718 via recrystallization-based grain boundary engineering induced by its residual stress

Metals containing abundant coherent twin boundaries (TBs) can improve corrosion resistance. Tailoring TBs in additive manufacturing (AM)-fabricated metallic materials with lower stacking fault energy, however, has proven impracticable because the traditional grain boundary engineering (GBE) involved in thermomechanical processing is not appropriate for AM-fabricated alloys with complicated geometric shapes. Here, the AM-fabricated Inconel 718 superalloy was successfully utilized to form abundant TBs induced by the intrinsic residual internal stresses, produced by AM processing via direct heat treatment. The microstructural characteristics and corresponding hot corrosion behaviors of different specimens – initial AM-fabricated, directly aged, and GBE-treated specimens – exposed to a mixed salt of 75 wt% Na2SO4 + 25 wt% NaCl at 650 °C were compared and analyzed systematically. The corrosion mechanisms affecting each of the specimens are discussed in detail. The obtained results reveal that the GBE-treated specimen has the most intact surface after the corrosion test, suffering minimum mass loss and having the shallowest corrosion layer depth, exhibiting optimal hot corrosion resistance. This optimal performance is mainly attributed to the penetration of S and O elements that were efficiently impeded by the TBs. This result holds implications for improving hot corrosion resistance in AM-fabricated metallic materials via directly GBE induced by residual stress.

Effect of Al on the low cycle fatigue deformation behavior and microstructure evolution of Fe–22Mn-0.6C TWIP steel

The dependence of low cycle fatigue (LCF) behavior and microstructure evolution of Fe–22Mn-0.6C twinning-induced plasticity (TWIP) steel on the alloying element Al has been investigated under fully reversed total strain amplitude control with a nominal strain rate of 0.006 s−1 and strain amplitudes ranging from 0.002 to 0.010 at room temperature. The results indicate a strong dependence of LCF response and evolved microstructure on the addition of Al, owing to its effect on the stacking fault energy (SFE). At all strain amplitudes, the 3Al steel with a higher SFE exhibits a visibly lower cyclic hardening and a higher cyclic softening, resulting in a lower cyclic yield strength than the 0Al steel. As compared with the 0Al steel, the relatively higher SFE of the 3Al steel causes higher accumulated plastic strain, decreased slip planarity and weaker reversibility of dislocations, thereby decreasing the fatigue life. The optical microstructure is featured by increase in slip band density with increasing strain amplitude for both steels. However, the slip band density of the 3Al steel is higher than that of the 0Al steel. Moreover, cyclic loading promotes the formation of dislocation cells, rough labyrinths as well as planar dislocation arrays. Deformation twins are observed only in the 0Al steel with a visible lower critical twinning stress due to its low SFE as compared to the 3Al steel.

Dual heterogeneous structure enabled ultrahigh strength and ductility across a broad temperature range in CrCoNi-based medium-entropy alloy

Developing alloys with exceptional strength-ductility combinations across a broad temperature range is crucial for advanced structural applications. The emerging face-centered cubic medium-entropy alloys (MEAs) demonstrate outstanding mechanical properties at both ambient and cryogenic temperatures. They are anticipated to extend their applicability to elevated temperatures, owing to their inherent advantages in leveraging multiple strengthening and deformation mechanisms. Here, a dual heterostructure, comprising of heterogeneous grain structure with heterogeneous distribution of the micro-scale Nb-rich Laves phases, is introduced in a CrCoNi-based MEA through thermo-mechanical processing. Additionally, a high-density nano-coherent γ' phase is introduced within the grains through isothermal aging treatments. The superior thermal stability of the heterogeneously distributed precipitates enables the dual heterostructure to persist at temperatures up to 1073 K, allowing the MEA to maintain excellent mechanical properties across a wide temperature range. The yield strength of the dual-heterogeneous-structured MEA reaches up to 1.2 GPa, 1.1 GPa, 0.8 GPa, and 0.6 GPa, coupled with total elongation values of 28.6 %, 28.4 %, 12.6 %, and 6.1 % at 93 K, 298 K, 873 K, and 1073 K, respectively. The high yield strength primarily stems from precipitation strengthening and hetero-deformation-induced strengthening. The high flow stress and low stacking fault energy of the dual-heterogeneous-structured MEA promote the formation of high-density stacking faults and nanotwins during deformation from 93 K to 1073 K, and their density increase with decreasing deformation temperature. This greatly contributes to the enhanced strain-hardening capability and ductility across a wide temperature range. This study offers a practical solution for designing dual-heterogeneous-structured MEAs with both high yield strength and large ductility across a wide temperature range.

Manipulating Stacking Fault Energy to Achieve Crack Inhibition and Superior Strength-Ductility Synergy in an Additively Manufactured High-Entropy Alloy.

Additive manufacturing (AM) is a revolutionary technology that heralds a new era in metal processing, yet the quality of AM-produced parts is inevitably compromised by cracking induced by severe residual stress. In this study, a novel approach is presented to inhibit cracks and enhance the mechanical performances of AM-produced alloys by manipulating stacking fault energy (SFE). A high-entropy alloy (HEA) based on an equimolar FeCoCrNi composition is selected as the prototype material due to the presence of microcracks during laser powder bed fusion (LPBF) AM process. Introducing a small amount (≈2.4 at%) of Al doping can effectively lower SFE and yield the formation of multiscale microstructures that efficiently dissipate thermal stress during LPBF processing. Distinct from the Al-free HEA containing visible microcracks, the Al-doped HEA (Al0.1CoCrFeNi) is crack free and demonstrates ≈55% improvement in elongation without compromising tensile strength. Additionally, the lowered SFE enhances the resistance to crack propagation, thereby improving the durability of AM-printed products. By manipulating SFE, the thermal cycle-induced stress during the printing process can be effectively consumed via stacking faults formation, and the proposed strategy offers novel insights into the development of crack-free alloys with superior strength-ductility synergy for intricate structural applications.

Improving ductility of high strength nanotwinned steel with reverse transformation of epsilon martensite inside nanotwin lamellae

In this work, the reverse transformation of ε-martensite located inside nanotwin lamellae has been introduced to improve the ductility of a high-strength Fe–Mn–C steel with a high density of nanotwins. The steel was designed to have a low stacking-fault energy (SFE, 17.8 mJ/m2) to introduce high density of nanotwins through pre-deformation. Meanwhile, the fine ε-martensite was also obtained in nanotwin lamellae. The steel was strengthened significantly, with an increase in yield strength from 357 to 1275 MPa by the introduction of nanotwins. A subsequent intermediate annealing was applied to control the reverse phase transformation from ε-martensite to austenite to enhance the deformation ability of the nanotwinned steel (rising tensile elongation from 5 to 16%). The nanotwins with a width of 32 nm on average were stable during the heat treatment. The high strength was retained because the size of the austenite transformed from ε-martensite was restrained by the stable nanotwins. This strategy holds promise and can be widely applied to alloys with low SFE.

Formation of intracrystalline deformation twins in austenitic Mn-steel at the early stage of plastic deformation

In austenitic Mn-steels with low stacking fault energy, the deformation twin is known to play an important role in plastic deformation. Usually, the position grain boundary is preferred to observe and investigate the formation process of the deformation twin, while other suitable formation positions may be neglected. Here, high-resolution transmission electron microscopy is used to observe and characterize the formation of intracrystalline twins in 120Mn13 steel at the early stage of tensile plastic deformation at the atomic scale. The result shows that intracrystalline twins nucleate through overlapping stacking faults generated by three different perfect dislocations dissociating on consecutive {111}-type planes, which is different from twin nucleation mechanisms that have been proposed. Subsequently, they become large-sized intracrystalline twins or twin bands throughout the whole grain by twin nuclei growing themselves and connecting to adjacent twin nuclei or existing twins in the same growth direction. Intracrystalline twins are mainly formed in three positions, namely near the grain boundary, at the end or side of existing twins. The stacking fault sources of intracrystalline twins at different positions are different.

Reconsideration of the dislocation arrest model for dynamic strain aging in C-bearing high Mn steel with low stacking fault energy

In the present study, we investigated the behavior of type A serration in the tensile flow curves measured at temperatures ranging from 273 K to 323 K with a strain rate of 1 × 10−3 /s, using high Mn steels with varying N contents. As a result, it was found that the critical engineering strain for the onset of type A serrations (ecA) increased with an increase in the N content at a given tensile temperature. This finding could not be explained by the conventional dislocation arrest model, which has been used to account for type A serrations occurring in C-bearing high Mn steels without N. Therefore, we attempted to explain the result by introducing the dynamic formation of obstacles to dislocation slip, such as mechanical twins and Lomer-Cottrell locks, during tensile deformation, a factor not considered in the conventional dislocation arrest model. However, the specific reason for the increase in the ecA value due to the addition of N was not elucidated. Therefore, we modified the dislocation arrest model based on the concept that the combination and cross-slip of screw partial dislocations, which accumulate at the obstacles, become more favorable due to an increase in stacking fault energy resulting from the addition of N. The modified dislocation arrest model successfully explained the influences of not only N content but also strain rate and tensile temperature on the ecA value in both C-bearing high Mn steels with and without N.

Achieving exceptional combination of strength and ductility in α+β diphase brass with harmonic structure

Heterogeneous structures are an effective way to give materials excellent combined strength-ductility properties. In this study, Cu–Zn–Al–Fe alloys were prepared by homogenizing and hot rolling-annealing, and an α+β diphase brass with harmonic structure was obtained by adjusting the content of Zn. The microstructure and mechanical properties of Cu-xZn-4Al-2.8Fe (x = 14, 20, 22.5, 24, wt%) were systematically investigated. The Cu–Zn–Al–Fe alloy has an α single-phase matrix at 14 wt% Zn and an α+β diphasic matrix at 20, 22.5, and 24 wt% Zn, all uniformly distributed with nano β(FeAl). A large amounts of twins are produced after rolling in α phase that has a low stacking fault energy. The Cu–20Zn–4Al-2.8Fe alloy exhibits a unique harmonic structure of the α-phase soft cores embedded in α+β biphasic hard shells. This alloy exhibits an excellent strength-ductility combination at room temperature, possessing an ultimate tensile strength of 473.7 MPa while maintaining a total elongation of 50.7%. Increases total elongation by 30.3% while maintaining high strength compared to homogeneous alloys (22.5 wt% Zn). While α single-phase alloy (14 wt% Zn) exhibits excellent plasticity (total elongation of 58.0%), their strength is not satisfactory (ultimate tensile strength of 419.7 MPa). In contrast, too much Zn (24 wt% Zn) produces a high proportion of β phase, which exhibits high strength (ultimate tensile strength of 507.9 MPa) and relatively poor plasticity (total elongation of 22.8%). Overall, the Cu–20Zn–4Al-2.8Fe alloy with a harmonic structure achieves excellent overall mechanical properties due to twinning, precipitation strengthening, and hetero-deformation induced (HDI) strengthening. This study provides an essential reference for designing heterogeneous structures of brass alloys.

Atomistic modeling of idealized equal channel angular pressing process

Severe plastic deformation (SPD) processes are forming techniques that impose large plastic strains to achieve ultra-fine grained and nanocrystalline microstructures. The refined microstructure results in a significant increase in strength and in many cases without a considerable loss in ductility. Despite their long existence, a comprehensive understanding of the deformation and grain refinement mechanisms during SPD is still lacking. Atomistic simulations that are regularly used to obtain insights into material behavior have rarely been used to study SPD processes. In this work, we use large scale atomistic simulations of the molecular statics/dynamics kind to model the equal channel angular pressing (ECAP) process, a specific SPD process. Three different materials—Al, Ni and Cu—are used to model high, medium and low stacking fault energy materials. Large simulation cells are used to facilitate grain refinement at the nanoscale. The simulations are carefully analyzed in terms of stress–strain behavior, dislocation activity and grain refinement. All samples show the formation of deformation twins at the nanoscale, which generally detwin at increased strains via dislocation twin interactions. A significant number of stair-rod dislocations form via dislocation–dislocation interactions and are present at low angle grain boundaries in the early stages of deformation. Such stair-rod dislocations also result in the formation of stacking fault tetrahedra which are present in significant numbers in all samples. Finally, difficulties in studying grain refinement at very large strains in atomistic simulations are discussed.

Laser shock-induced gradient twinning microstructure in AZ31B alloy

Magnesium alloys are highly promising in biodegradable materials for medical applications. However, their applications are limited by weaknesses in mechanical strength and corrosion resistance. In recent years, advancements in a novel laser method, Laser Shock Peening (LSP), have been explored. Researchers suggest that LSP can induce surface compressive stresses and induce changes in residual stress and grain size gradients, thereby enhancing the material's fatigue resistance, corrosion resistance, and resistance to stress corrosion cracking. However, there is ongoing debate about whether LSP treatment can, in effect, create a gradient microstructure. In this study, we focused on the AZ31B alloy, notable for its dense hexagonal close-packed (HCP) crystal structure. This material is particularly interesting because, due to its low stacking fault energy, it is more prone to twinning deformation than to dislocation slip when it undergoes plastic deformation. To analyze the changes wrought by LSP, we employed optical microscopy (OM), electron backscatter diffraction (EBSD), and X-ray diffraction (XRD) for examining the microstructures both before and after LSP treatment. Our findings revealed that LSP treatment refined the grain size, leading to a gradient distribution. In addition, we observed a direct correlation between the volume fraction of twinning and grain size. In contrast, the geometrically necessary dislocation (GND) density exhibited an inverse relationship. By measuring hardness and residual stress in the region affected by LSP, we determined that LSP could introduce a layer of plastic deformation up to a depth of 800–1000 μm. We also established a link between the gradient microstructure and hardness and provided a thorough discussion on the types of twinning and the mechanisms behind the induction of gradient microstructure on the surface.

Twin spacing and grain size dependent tensile deformation mechanism of a nano-ploycrystalline Ni-based alloy

It is easy to form twins in Ni-based wrought superalloys with low stacking fault energy, but the effect of grain size and twin spacing on mechanical properties in nano-ploycrystalline Ni-based alloys is rarely studied. Based on the composition of a novel Ni-based wrought superalloy, molecular dynamics simulations were used to study the effect of grain size and twin spacing on the deformation behavior of the Ni57Cr19Co19Al5 alloy. The results show that the elastic modulus and tensile strength of the nano-polycrystalline Ni57Cr19Co19Al5 alloy exhibit clear grain size dependence. As the grain size exceeded 16 nm, the elastic modulus remained unchanged. The tensile strength and grain size satisfy the Hall–Petch relationship, and the dislocation motion dominates the plastic deformation. For the grain size below 16 nm, the elastic modulus decreases as the grain size decreases. The tensile strength and the grain size exhibit an inverse Hall–Petch relationship. The grain boundary sliding and grain torsion mechanisms dominated plastic deformation in the nano-polycrystalline Ni57Cr19Co19Al5 alloy without twin. In the nano-polycrystalline Ni57Cr19Co19Al5 alloy containing twins, the twin boundaries inhibited the torsion of grains, and grain boundary sliding dominated plastic deformation.

Diffusion in ultra-fine-grained CoCrFeNiMn high entropy alloy processed by equal-channel angular pressing

Grain boundary diffusion in severely plastically deformed (SPD) CoCrFeMnNi high entropy alloy (HEA) has been studied by applying the tracer diffusion technique. After two passes of equal channel angular pressing (ECAP), three untra-fast diffusion paths in ECAP-processed CoCrFeMnNi HEA were distinguished, which were identified with twin boundaries, high-angle grain boundaries and porosity defects. The enhanced diffusivity is induced by a high strain localization in the vicinity of interfaces in a deformation-induced non-equilibrium state that is correlated with the pronounced deformation twinning due to the low stacking fault energy of the material.