Strengthening Phase Research Articles

Structural and property regulation of double ceramic phase–reinforced AlCoCrFeNiTiZr–based high entropy alloy coatings by pulsed–wave lasers

In-situ synthesis ZrC and TiC reinforced AlCoCrFeNiTiZr–based high entropy alloy (HEA) coatings were successfully synthesized on R60702 using pulsed–laser cladding. The effects of pulse frequency (5, 50, 500, and 5000 Hz) on microstructure evolution, microhardness, wear resistance, and corrosion resistance were investigated. The results demonstrate that the HEA coatings consists of phases including BCC, HCP, and metal carbides (MC). The phase composition and proportion are influenced by changes in pulse frequency. At pulse frequencies of 5 and 50 Hz, the predominant MC phase is ZrC. As the pulse frequency increases, it transitions to a coexistence of ZrC + TiC before ultimately becoming predominantly TiC. Concurrently, the size of the ceramic phase and the proportion of the HCP phase initially decrease, then increase. A pulse frequency of 500 Hz yields optimizations in microhardness, wear resistance, and corrosion resistance. The favorable mechanical properties are attributed to the synergistic effect of solid solution strengthening, fine crystal strengthening, and ceramic phase strengthening. The optimal corrosion resistance is due to the formation of a stable passivation film while local corrosion and galvanic corrosion are weakened.

Synchronously enhanced printability and properties of additively manufactured nickel-based superalloys via alloying minor Sc

As major forming elements of γ′ strengthening phase, Al and Ti are critical for achieving superior properties of Ni-based superalloy. However, Al + Ti over 6 wt% leads to poor printability and cracking during additive manufacturing. In this work, the printability and properties of a nickel-based superalloy with Al + Ti reaching 7 wt% is synchronously improved via alloying minor Sc, the mechanism behind that is revealed by investigating the effects of Sc on the grain size, precipitation, and tensile fracture behavior of that nickel-based superalloy. This work provides a promising alternative method for optimizing the performance of superalloys prepared by additive manufacturing.

Importance of γ′ shearing in low‐cycle fatigue of a wrought superalloy

AbstractThe present study deals with the fatigue behavior of a wrought nickel‐based superalloy René 41. Uniaxial, fully reversed low‐cycle fatigue tests were conducted at room and elevated (800°C) temperatures under total strain control. Cyclic response was analyzed using the statistical theory of the hysteresis loop, and scanning and transmission electron microscopies were employed to study relevant damage mechanisms. At room temperature, cyclic deformation was found to localize to slip bands since the first cycle, and most slip bands were formed very early in the fatigue life. Hence, shearing of the strengthening phase, coherent γ′ precipitates, was found to be significant only in the first few cycles. At 800°C, fatigue life was affected by an environmental attack resulting in a surface oxide layer. Cyclic deformation was less localized; nevertheless, cyclic slip localization in persistent slip bands and resulting γ′ shearing contributed to cyclic softening throughout the fatigue life.

Toward the superior high-temperature strength of Al-5Fe alloy for powder bed fusion-laser beam: Stabilizing Al6Fe nanoprecipitate by Sc and Zr elements

Existing additively manufactured aluminum alloys exhibit unfavorable tensile strength above 200 °C due to the strengthening phase coarsening, microstructure instability and cracking. This paper designed a novel Al-5Fe-1Mg-0.6Sc-0.3Zr alloy for powder bed fusion using laser beam (PBF-LB) with tensile strength of 189 MPa at 400 °C, which is the highest value reported. The main strengthening phases of the alloy were Al6Fe particle and nano-scaled L12-Al3(Sc, Zr) precipitates. The exceptional high-temperature performance is attributed to high volume fraction (∼35%) of nanoprecipitates Al6Fe modified by Sc and Zr elements, showing enhanced thermal stability and refined particle dimension. The addition of Sc and Zr elements also significantly retards the phase transformation from Al6Fe to θ-Al13Fe4 and inhibits brittle θ phase growth during thermal exposure.

Effect of W on the Mechanical Properties and Tribological Behavior of CoCrFeNiWx Compositionally Complex Alloy

Introducing the hard second phase into soft matrix and reducing the grain size are key strategies to enhance the strength and wear performance of metallic alloys. Herein, to investigate the effect of hard second phase on the mechanical properties and tribological behavior of face‐centered‐cubic (FCC) CoCrFeNi compositionally complex alloy (CCA), a series of ultrafine‐grained CoCrFeNiWx (x = 0, 0.3, 0.5, and 1.0) CCAs with varying W contents are fabricated. The results show that the single FCC CCA transforms to the dual phase of FCC and μ phase after addition of W. With increasing W content, the hardness and yield strength show a linear increase due to the additional solid solution strengthening and secondary phase strengthening, but the fracture strain shows an opposite trend. Dry sliding wear tests show that both coefficients of friction and wear rates decrease with the W content. The wear mode changes from abrasive wear for CoCrFeNi CCA to multiple wear modes of abrasive wear, oxidative wear, and fatigue wear for W‐containing CCAs. These results suggest that adding W into the FCC CCA matrix could strengthen the FCC alloy and simultaneously improve wear performance.

Preparation of Al-Ti-Sc master alloys and refining effects on the 6016 aluminum alloy

The 6016 aluminum alloy has good plasticity but low strength. In this work, Al-Ti-Sc master alloy was prepared by thermite reduction method in order to obtain an effective grain refiner with a simplified preparation process and a reduced cost. The refining effects of the ternary master alloy on the 6016 aluminum alloy were checked to improve the strength and plasticity simultaneously. The chemical reactions during the preparation process of the Al-Ti-Sc master alloy was studied by thermodynamic software of HSC 6.0. The content of Sc and Ti in the master alloy reaches 2.48 wt% and 1.4 wt%, respectively, on proper experimental conditions, and the main phases of the master alloys are α-Al and Al3(Sc,Ti) phase. In the refined alloys, the average grain size can reach 27 μm, and the ultimate tensile strength and the elongation after fracture reaches 280 MPa and 35% in cast state, respectively. Compared to the pristine 6016 aluminium alloy, the significantly enhanced strength and good plasticity of the refined alloys contribute to the combined effects of grain refinement and precipitated phase strengthening. For the fracture of low doped alloys, originates from cleavage fracture mechanisms, and for the ones with high dosages, ductile fracture becomes dominant.

Effect of Al addition on the mechanical property and irradiation resistance of NbMoZr-based medium-entropy alloys

In this work, the Nb50Mo30Zr20 and Al5Nb50Mo30Zr15 alloys are successfully fabricated and the samples are irradiated by 5 MeV Xe+ ions at 350 °C and 750 °C. Room temperature compression results show that the addition of Al can effectively increase the compressive yield strength from ∼ 1288 MPa in NbMoZr alloy to ∼ 1703 MPa in AlNbMoZr alloy. The increase in strength is attributed to the solid solution strengthening, second phase strengthening and dendrite refinement strengthening due to the minor Al additions. After irradiation at 350 °C and 750 °C, the HCP-structured Zr phases precipitate in ternary NbMoZr alloy. In contrast, with the addition of Al atoms, the dendritic matrix of AlNbMoZr alloy can still maintain the BCC structure after irradiation, which exhibit a higher phase stability than NbMoZr alloy. Moreover, the Al suppress the growth of Xe bubbles and decrease the dislocation loops in AlNbMoZr alloy, as compared with those in the Al-free NbMoZr alloy. The relevant results can provide theoretical guidance for developing high-performance metals used in the field of advanced nuclear fuels.

Effects of temperature-induced variation of the second phase on the microstructure, texture and properties of Mg-RE-Zn alloys

In this paper, the Mg-9.32Gd-3.72Y-1.68Zn-0.72Zr (wt%) alloy has undergone three times of repetitive upsetting extrusion deformation. Alloys with different morphologies and distribution patterns of the second phase have been prepared by varying the deformation temperature in each pass. The effects of the second phase on microstructure, texture and mechanical properties are investigated. The results show that (i) the second phase, including Mg5Gd and LPSO phase, has an important effect on the dynamic recrystallization (DRX) behavior of the alloy. (ii) Appropriate lamella distance and block phase size can promote the activation of the slip system and effectively weaken the texture strength. (iii) The DT sample has an effective combination of fine grain strengthening and second phase strengthening due to the reasonable second phase distribution and size, which greatly improves the UTS and YS of the alloy.

Short study on mechanism of morphology change of γ′ precipitates in IN718 Plus

γ′ Ni3Al phase (L12 structure) strengthened superalloy has become an important strengthening phase in Ni based superalloys because of its excellent high-temperature service performance, and has been widely used. The process of γ′ phase precipitation has also received a lot of attention and research. However, most studies focused on its growth rate. There were few studies on the morphology transformation of γ′ phase, and the morphology transformation process is complex. The mechanism of γ′ phase transformation process was systematically analyzed in this paper. Firstly, through molecular dynamics calculation, the most stable morphology of the γ′ phase in the nickel matrix was obtained under ideal conditions. The stability of spherical precipitates is higher than that of cubic precipitates. When the temperature is greater than 800 K, the stability is more obvious.Then through the micro EDS analysis of the γ′ phase in the morphology transformation process, it was shown that the soft impingement phenomenon exists in the nickel base alloy with high γ′ phase volume fraction. Further, by the derivation of the formula of solid-state phase transformation, it was found that the growth rate of precipitate is directly proportional to the concentration gradient of Al in the matrix at the interface, while increases with the rising of the Al concentration in the matrix at the interface. Finally, the way and mechanism of soft impingement affecting the morphology transformation were analyzed. The precipitates formed by soft impingement are nearly cubic precipitates with rounded edges and corners.

Study of microstructure evolution and strengthening mechanisms in Mox(Nb3TaTi3Zr)100−x high-entropy alloys

A new series of high-entropy alloys denoted as Mox(Nb3TaTi3Zr)100−x, has been designed for aero-engine applications. The study focused on investigating the microstructural evolution and strengthening mechanisms of the alloys in response to varying Mo content. Results indicate that the alloys primarily display a BCC crystal structure. Notably, an FCC phase precipitates in the alloy when the Mo content reaches 30%. Furthermore, as the Mo content increases, the strength of the alloys significantly increases while their plasticity diminishes. The room-temperature yield strength of the alloys shows a substantial increase from 729 MPa (x = 0) to 1202 MPa (x = 25), while the yield strength at 1200 °C rises from 62 MPa (x = 0) to 498 MPa (x = 30). Concurrently, the microhardness of the alloys also increases from 247 HV (x = 0) to 471 HV (x = 30). The observed strengthening mechanisms include solid solution strengthening, fine grain strengthening, and precipitated phase strengthening.

Composition-dependent brittleness and ductility of the multicomponent phase (Fe, Cr)23(C, B)6 in Fe–Cr–B–C alloys: First-principles calculations and modeling

(Fe, Cr)23(C, B)6, as a strengthening phase in Fe–Cr–B–C alloys, has not been reported on the relationship between its properties and composition over the entire composition range. (Fe, Cr)23(C, B)6 tends to exhibit brittleness, which is difficult to regulate through traditional experiments. The mechanical properties of (Fe, Cr)23(C, B)6 phase in Fe–Cr–B–C alloy have been studied by first principles calculation. With the help of CALPHAD method, the distribution of elastic constant, modulus, hardness and fracture toughness in the whole component space was obtained, so that the suitable component with good wear resistance and strong toughness was obtained. The mechanical properties of (Fe, Cr)23(C, B)6 phase is better in the range of ∼0.4–0.6 at. % B and ∼0.5–0.7 at. % Cr. The mechanism of these differences is explained in terms of state density, bond length, population analysis and differential charge density, as the addition of boron and the increase in chromium content led to a significant increase in the formation of covalent bonds between metals and non-metals, in which these bonds play a decisive role. The combination of the first principles calculation and the CALPHAD model provides a feasible model for constructing the composition-property relationship of medium entropy compounds.

Microstructure and Tensile Properties of HPDC Mg–RE Alloys with Varying Y Additions

AbstractHigh-pressure die-casting Mg–2.6RE–xY (EW) alloys with Y contents between 0 and 3% (in wt%) were investigated for their microstructure and tensile properties. In the Y-containing alloy, the intermetallic phases at the grain boundaries consisted of skeletal Mg12RE phase, bulk Mg24Y5 phase and irregular Mg3Y phase, while {011} twins were observed in the Mg12RE phase. The yield strength was improved by Y addition at both room temperature and high temperatures. Compared with Y-free alloy, the yield strength of 3% Y alloy increased from 143.1 to 174.8 MPa and improved by 22.2% at room temperature, while it was increased from 72.2 to 104.6 MPa and enhanced by 44.9% at 300 °C. The area fraction of intermetallic phase increased dramatically from 14.5 to 18.4% with 3% Y addition. Second phase strengthening was the major contributor to the yield strength increase at ambient temperature. The increment of the area fraction of the high-thermally stable Mg–RE intermetallic phases with Y addition contributed to the consequent improvement in yield strength at high temperatures. At ambient temperature, the mechanism for the fracture of EW alloys was a ductile and quasi-cleavage fracture blend.

Effects of heat treatment cooling methods on precipitated phase and mechanical properties of CoCrFeMnNi–Mo5C0.5 high entropy alloy

C and Mo in the form of solid solution atom or compound phase is distributed in CoCrFeMnNi high entropy alloy (HEA), which have the effects of solution strengthening or second phase strengthening. CoCrFeMnNi–Mo5C0.5 HEA were prepared by adding C and Mo elements to CoCrFeMnNi HEA, and then which heat treatment were carried out by furnace-cooling, air-cooling and water-cooling respectively. the microstructure and phase composition of as-cast or heat treated CoCrFeMnNi–Mo5C0.5 HEA were examined by scanning electron microscopy (SEM), energy dispersive spectrometry (EDS) and X-ray diffraction (XRD), the mechanical properties of as-cast or heat treated CoCrFeMnNi–Mo5C0.5 HEA were tested by the tensile test and hardness test, and the effects of heat treatment cooling methods on precipitated second phase and mechanical properties of CoCrFeMnNi–Mo5C0.5 HEA were investigated. The results show that precipitated second phase in CoCrFeMnNi–Mo5C0.5 HEA is MC phase, which is rich in Mo, Cr and C elements. With change of heat treatment cooling methods from furnace-cooling, air-cooling to water-cooling respectively, heat treatment cooling rate is increased. With increase of heat treatment cooling rate, the amount and size of precipitated second phase are all decreases, and the position of second phase precipitation changes from grain boundaries to intragranular. The tensile strength and elongation of heat treatment water-cooled CoCrFeMnNi–Mo5C0.5 HEA are 739 MPa and 41% respectively, which are realizes the simultaneous increased of strength and plasticity. With increase of heat treatment cooling rate, the hardness of CoCrFeMnNi–Mo5C0.5 HEA decreases, the uniform plastic deformation and the elongation are all increases, and the plasticity increase. The fractures of as-cast, heat treatment furnace-cooled, air-cooled and water-cooled CoCrFeMnNi–Mo5C0.5 HEA are all brittle fracture with cleavage characteristics, and the plastic deformation occurs mainly in the uniform plastic deformation stage. The fracture mode of as-cast CoCrFeMnNi–Mo5C0.5 HEA is intergranular fracture, the fracture mode of heat treatment furnace-cooled, air-cooled and water-cooled CoCrFeMnNi–Mo5C0.5 HEA are all transgranular fracture.

Tailoring Multiple Strengthening Phases to Achieve Superior High-Temperature Strength in Cast Mg-RE-Ag Alloys.

Mg alloys with excellent high-temperature mechanical properties are urgently desired to meet the design requirements of new-generation aircraft. Herein, novel cast Mg-10Gd-2Y-0.4Zn-0.2Ca-0.5Zr-xAg alloys were designed and prepared according to the advantages of multi-component alloying. The SEM and XRD results revealed that the as-cast microstructures contained α-Mg grains, β, and Zr-containing phase. As Ag rose from 0 wt.% to 2.0 wt.%, the grain size was refined from 40.7 μm to 33.5 μm, and the β phase significantly increased. The TEM observations revealed that the nano-scaled γ' phase could be induced to precipitate in the α-Mg matrix by the addition of Ag. The stacking sequence of lamellar γ' phases is ABCA. The multiple strengthening phases, including β phase, γ' phases, and Zr-containing particles, were effectively tailored through alloying and synergistically enhanced the mechanical properties. The ultimate tensile strength increased from 154.0 ± 3.5 MPa to 231.0 ± 4.0 MPa at 548 K when Ag was added from 0 to 2.0 wt.%. Compared to the Ag-free alloy, the as-cast alloy containing 2.0 wt.% Ag exhibited a minor reduction in ultimate tensile strength (7.0 ± 4.0 MPa) from 498 K to 548 K. The excellent high-temperature performance of the newly developed Mg-RE-Ag alloy has great value in promoting the use of Mg alloys in aviation industries.

Effect of Al2O3 on Microstructure and Corrosion Characteristics of Al/Al2O3 Composite Coatings Prepared by Cold Spraying

Cold spraying was used to prepare Al/Al2O3 composite coatings. The Al2O3 content was controlled to increase the mechanical property and corrosion resistance of the composite coating. The inclusion of Al2O3 particles results in considerable plastic deformation of Al particles and grain size refinement in the coating. Additionally, the coating’s surface roughness decreased from 24.63 μm to 9.02 μm, and the porosity decreased from 6.34% to 2.07%. The increase in microhardness of the composite coatings was attributed to the combined effect of residual compressive stress, second phase strengthening of Al2O3, and plastic hardening of Al particles. The electrochemical test results indicate that the mass fractions of Al2O3 significantly affected the corrosion resistance of the Al/Al2O3 composite coating. Compared to the Al coating, the composite coating exhibited improved corrosion resistance, with a reduction in corrosion current density from 1.09 × 10−3 A/cm2 to 2.67 × 10−6 A/cm2 and an increase in corrosion potential from −1.57 V to −1.14 V. However, when the alumina particle content exceeded 17.7%, it led to more Al2O3 particle breakage, increasing the weak bonding interfaces in the composite coating, and consequently reducing its corrosion resistance.

From rhetoric to reality: shaping doctoral education in China for global higher education

PurposeAlthough doctoral education has experienced substantial development in recent decades, it remains an elite, hence fragile, dimension of university policy and practice. This study aims to articulate perspectives to guide the next phase of strengthening and growth.Design/methodology/approachWorking from theoretical and empirical research conducted in China, including scholarship on workforce ecosystems, education design and the student experience, this study contributes a framework with qualitative insights which clarify the goals and experiences of doctoral education in ways that will render it more relevant, effective and contributing.FindingsThe paper identifies areas for doctoral reform to ensure career readiness, including three distinctive outcomes and four indispensable experiences.Originality/valueThis study advances a doctoral design framework which can render transparent the substance of programs and prompt program coordinators to develop and ensure career relevance.

Enhancing tensile properties of laser additive manufactured FeCoNiCrMn high entropy alloy via adding Fe-based metallic glass

It has always been difficult to significantly improve the tensile strength of FeCoNiCrMn high entropy alloy (HEA) by traditional technical methods. Here, high-strength Fe-based metallic glass (MG) was precisely selected as the strengthening phase to reinforce the mechanical properties of FeCoNiCrMn HEA fabricated by laser additive manufacturing (LAM) technology. The results showed that although the addition of Fe-based MG with 5 wt% did not change the original phase composition of HEA, it facilitated grain refinement to a great extent. Of special significance was that the strength and ductility of HEA-MG exhibited a synergistic enhancement (σy, σUTS and εf were increased by 23.8 %, 28.4 % and 31.0 %, respectively) after Fe-based MG addition, deriving from the grain refinement, increased the dislocation density and formation of deformation twins.

Precipitation kinetics of γ′ and γ′′ particles in Inconel 718 and its influence on mechanical properties

The as-received state of Inconel 718 showcases a γ austenitic structure containing δ intergranular precipitates and a blend of (Nb,Ti)C type carbides. Furthermore, examination via transmission electron microscopy identified γ′′ precipitates (elongated disks) and γ′ precipitates (spherical in shape), with γ′′ being the prevailing phase. After quenching at 990 °C for 30 min, the structure comprises an fcc γ matrix hosting randomly dispersed (Nb,Ti)C carbides. Additionally, the TEM examination of the quenched state showed an absence of the δ phase and γ′′ and γ′ precipitates. The precipitation of γ′′ and γ′ phases was studied in Inconel 718 alloy using specimens which were subjected to isothermal aging for various durations at temperatures between 600 and 750 °C and were previously quenched in water at 990 °C for 30 min. The tensile and the micro-hardness mechanical properties were studied for aging at 680 and 750 °C at 4, 50 and 100 h aging duration. The grain growth kinetic of γ′′ and γ′ precipitates has been analyzed following the power–law relationship Dn= Kt and the rate constant K = K0exp−QRT. The optimum grain growth exponent n of γ′′ and γ′ phases has been determined as equal to 2.3. The activation energy values for γ′′ and γ′ coarsening have been determined as equal to 209 kJ mol−1 and 139 kJ mol−1, respectively. Based on the experimental results, a mathematical model was established to describe the grain growth behavior of the studied Inconel 718 alloy for different tempering temperatures and holding times. The predicted grain size growth is in good agreement with the measured one. For aging at 680 °C, the optimum aging time which corresponds to the highest value of yield strength (1164 MPa) and Vickers micro-hardness (500) due to γ′′ strengthening phase, was determined as 50 h. Nonetheless, when subjected to aging durations surpassing 50 h at 750 °C, the reduction in both yield strength and micro-hardness can be attributed primarily to the coarsening of γ′′ precipitates, followed by a decrease in the volume fraction of the γ′′ phase. This reduction is a result of the concurrent increase in the volume fraction of the δ phase. For γ′′ particle size lower or equal to 35 nm, strengthening is governed by the shearing mechanism. Beyond 35 nm γ′′ particle size, the γ′′ precipitates are crossed preferably by bypassing mechanism. A relationship between the 0.2% yield strength and the Vickers micro-hardness was determined.

Influence of Cu/Mg ratio and content on heat-resistance of Al–Cu–Mg alloys

Heat-resistant Al alloys used in such as aerospace, transportation fields are attracting more and more attention in recent years. Within Al alloy families, Al–Cu–Mg alloys have shown promising heat resistance properties. This work aims to investigate the influence of Cu/Mg ratio and content on the heat resistance of Al–Cu–Mg alloys, based on alloys of Al–4.5Cu–2.5 Mg (referred to as alloy A), Al–4.0Cu–2.2 Mg (alloy B) and Al–4.5Cu–1.6 Mg (alloy C). The alloys A and B possessed approximate Cu/Mg ratio, and they also exhibited nearly identical hardness retention rate during exposure at 200 °C. After 200 h, the rate is ∼75 %, though alloy A showed higher hardness (105 vs. 102 HBW) due to higher Cu, Mg content. In contrast, alloy C with a higher Cu/Mg ratio was less heat-resistant, with hardness retention rate of ∼70.5 % after 200 h exposure. Nano-sized S′(Al2CuMg) precipitate was main strengthening phase for the three alloys. Also, micron and submicron Al2CuMg particles could be formed with increase of Cu and Mg contents, which contributed a lot to yield strength for T6 heat-treated alloys, but slight contribution after exposure at 200 °C for 200 h. The degradation of mechanical properties during heat exposure can be attributed to the transformation and coarsening of S′ precipitates. In alloys with lower Cu/Mg ratio, there was excess Mg dissolved in Al matrix, which reduced Cu solubility in α-Al, and then slowed diffusion flux of Cu element, thus inhibited coarsening of Al2CuMg phase.

Evolution of Microstructure and Mechanical Properties of Novel Al-Mg-Mn-Ag-Cr-Zr Alloy

In order to reinforce the mechanism of Ag in 5xxx aluminum alloys with low magnesium, research on the microstructure and mechanical properties of an Al-Mg-Mn-Ag-Cr-Zr alloy was conducted using optical microscopy (OM), scanning electron microscopy (SEM), transmission electron microscopy (TEM), hardness measurement, and tensile testing. The as-cast microscopic structure of the alloy comprises the Al6(Mn, Fe) phase and the T-Mg32(Al, Ag)49 phase. Changes in the characteristics of the investigated alloy were clear during the aging process. Based on the findings obtained from TEM and SAED analysis, it was evident that the predominant strengthening phase during the peak-aged stage is the β″ phase, observed when the alloy is aged for 24 h at 160 °C. The β″ phase had a L12-type crystal lattice architecture and presented a completely coherent relevance with the Al-matrix. The lattice parameter, a, of the β″ phase was 0.408 nm. The mechanical properties of the peak-aged alloy increased greatly as compared to the as-quenched alloy. The tensile strength exhibited a rise from 410 MPa to 449 MPa, representing a 9.5% increase, while the yield strength demonstrated an increase from 185 MPa to 273 MPa, indicating a significant enhancement of 47.5%. The method used in the present study has solved the problem of 5xxx aluminum alloys not being heat treatable for strengthening to a significant degree, considerably improving the alloy strength. In addition, new methods and foundations for exploiting new-type Al-Mg based alloys and developing high-strength aluminum alloys are provided in this study.