Precipitates In Matrix Research Articles

The influence of minor additions of Y, Sc, and Zr on the microstructural evolution, superplastic behavior, and mechanical properties of AA6013 alloy

Alloy AA6013 (Al-Mg-Si-based aluminum alloy) is of particular interest to the aerospace and automotive industries because of its attractive combinations of properties, however, accelerated grain growth at elevated temperatures limits its superplastic formability. The motivation for this study was to refine grain structure and control grain growth at elevated temperature in order to eliminate the lack of superplasticity in the alloy. For this reason, minor additions of Y, Sc, Zr were considered and their influence on the microstructural evolution, superplastic deformation behavior, and room temperature mechanical properties of a novel AA6013-type alloy was studied. A noticeable refinement of as-cast grain structure was observed due to the co-effect of Sc, Zr, Y additions. It was demonstrated that the Mg2Si phase and Y-bearing phases were formed during solidification of the studied alloys. The phases of silidification origin were fragmented during thermo-mechanical treatment led to the near uniform distribution of coarse particles of 0.5–0.8 µm size in the matrix. The coarse particles caused grain refinement during the superplastic deformation due to the particle stimulated nucleation (PSN) effect. In the alloy containing yttrium, during the decomposition of the aluminum-based solid solution supersaturated by Y, Zr, Sc, the following two precipitation mechanisms were involved: continuous precipitation resulting in the formation of nanoscale L12 phase dispersoids distributed homogeneously throughout the aluminum matrix and discontinuous precipitation that caused fan-shaped aggregations of the same phase near the high-angle grain boundaries. The nanoscale continuously-formed dispersoids retarded the recrystallization and dynamic grain growth during superplastic deformation due to Zenner pinning mechanism. Both PSN and Zenner pinning effects led to the grain refinement and achievement of superplasticity. The maximum elongation of 470% was observed under the test condition of T = 520 °C and ɛ.= 1 × 10−3 − 5 × 10−2 s −1. The room temperature tensile test revealed the following maximum characteristics of the sheet of the alloy with Y additions: yield strength of 330 MPa, ultimate tensile strength of 375 MPa, and elongation at fracture of 10%.

An extended tensile flow curve model for carburized steels

An extended tensile flow curve model is derived for quenched-tempered as-carburized steels. It comprises a theoretical formula for calculating the yield strength of tempered martensite and a dislocation based strengthening theory. Precipitates transition in different tempering durations were taken into account, and an impact factor m was implemented to adjust the effect of confined precipitates in martensite matrix. The effective grain size dα′ evolution on tensile deformation behavior was taken into account to modify the tensile flow curve calculation as well. Favorable agreement was obtained between experimental and theoretical results. By means of this manner, it is feasible to evaluate the effect of microstructure evolution on strength and calculate the tensile flow curve, in terms of composition with defined treatment process.

Advanced positron annihilation studies of CuCrZr alloys

The influence of heat treatment (HT) on precipitate sizes and densities in CuCrZr alloy has previously been investigated by transmission electron microscopy (TEM). In this work, we studied the effect of HT on the defect structure in non-irradiated CuCrZr alloy using positron annihilation spectroscopy (PAS). Results obtained by PAS were compared with the results achieved by TEM. In the PAS measurements, a precise-defined long defect lifetime τ2 was observed with a basically constant value, while its intensity I2 exhibited strong dependency on the HT. Thus, a clear influence of the applied HT on the defect microstructure of CuCrZr alloy was observed. The measured defect lifetime τ2 parameter was associated to the creation of the vacancy-type defects at the precipitate matrix interface. We assume that it arises from the lattice mismatch (matrix, dislocations and precipitates). Further, the dependency of the specific trapping rate on the precipitate radius rppt was estimated and compared to theoretical values based on the diffusion-limited trapping and transition limited trapping models. These results are the base for future detailed studies of CuCrZr alloys after fast neutron irradiation treatment in connection to development of ITER or GenIV suitable materials.

Strengthening-toughening mechanism of cost-saving marine steel plate with 1000 MPa yield strength

One kind of cost-saving marine steel plate with 1000 MPa yield strength was successfully processed based on the alloying concept of nano-particles precipitation in a lath martensitic matrix. The conventional quenching and tempering heat treatment was adopted to optimize the mechanical properties. The experimental steel with lower alloy content exhibited excellent performance, i.e., the yield strength above 1030 MPa at room temperature, and the impact energy above 69 J at −40 °C. The microstructural evolution, precipitation behavior and dislocation density were systematically studied by optical microscopy, field emission scanning electron microscopy, X-ray diffraction and transmission electron microscopy. It was shown that the high strength resulted from grain refinement, dislocation strengthening, solid solution strengthening and precipitation strengthening. The role of every strengthening mechanism was quantitively evaluated so that the yield strength could be accurately estimated. Base on this study, it could be concluded that the precipitation strengthening had a significant contribution to yield strength. In addition, the excellent impact toughness of the steel was attributed to its unique microstructure characteristics of fine film-like stable austenite and delamination structure.

Effects of Remineralizing Agents Based on Calcium Phosphate, Sodium Phosphate, or Sodium Fluoride on Eroded Cervical Dentin.

To evaluate the effect of remineralizing agents on collagen matrix pattern, precipitate formation, and dentinal tubule obliteration in eroded cervical dentin. One hundred bovine cervical dentin specimens were previously eroded (0.6% hydrochloric acid, pH 2.3, 5 minutes) and then randomized into five groups (n=20): G1, control (without treatment); G2, Desensibilize Nano P (FGM); G3, MI Paste Plus (Recaldent); G4, Regenerate (NR-5); and G5, Desensibilize KF 2% (FGM). These treatments were applied in four sessions with 7-day intervals. During this period, the samples were subjected to an erosive challenge with orange juice (pH 3.8, 5 minutes). The specimens were analyzed by polarized light microscopy with picrosirius red staining, scanning electron microscopy (SEM), and energy-dispersive X-ray spectroscopy (EDX). The G3 showed a higher concentration of type I collagen than G2 and G5 (p<0.05). The G3 showed greater formation of surface precipitates than that of G1 and G5 (p<0.05). In addition, G4 and G5 showed a greater number of open dentinal tubules than that of G3 (p<0.05). Calcium phosphate-based remineralizing agents have shown to be a promising alternative treatment for preventing deleterious effects on the eroded dentin collagen matrix. In addition, they promoted precipitate formation and dentinal tubule obliteration on the eroded dentin.

Influence of different rolling processes on microstructure and strength of the Al–Cu–Li alloy AA2195

The influence of different rolling processes on precipitation behaviour, crystallography texture, grain morphology, and their consequent effects on tensile properties for Al–Cu–Li alloy AA2195 was investigated in the present work. The H-T8 samples (hot rolled ​+ ​T8) presented better tensile strength and ductility (with serious strength anisotropy) than the HC-T8 samples (hot rolled ​+ ​cold rolled ​+ ​T8), due to their different microstructures and textures. The higher dislocation density was found in the H-T8 samples, which promoted the nucleation of main strengthening phase T1 in the matrix and suppressed the grain boundary precipitation, resulted in better strength and ductility. The increase of the dynamic recovery (DRV) during hot rolling enhanced the generation of Brass texture, and brought serious strength anisotropy. The cold rolling was performed after the hot-rolling process for the HC-T8 samples which increased deformation energy and resulted in full recrystallization of the deformed microstructure during the following solution treatment. The formation of recrystallized microstructure reduced the dislocation density and the heterogeneous precipitate nucleation positions which limited the strengthening phase precipitation in matrix and accelerated the precipitation along grain boundaries, resulted in fewer T1 precipitates, coarse grain-boundary precipitates (GBPs), and wider precipitate-free zones (PFZs). The localized strain may be concentrated on the grain boundary to induce the dislocation pile-up, breaking of the GBPs, and intergranular fracture during stretching.

Microstructure and mechanical properties of a continuous carbon-gradient sheet steel

To take advantage of the high strength of high-carbon martensitic steel and simultaneously avoid insufficient plasticity, a novel continuous carbon-gradient sheet steel (CGSS) with a high-carbon surface and medium-carbon core was developed as a gradient material using surface carburizing and warm rolling. An exceptional strength–ductility combination was achieved. On the premise of carbides precipitation in high-carbon martensitic matrix, tempered CGSS at 200 °C exhibits excellent mechanical property with an ultimate tensile strength of 2440 MPa and a total elongation of 4.6%. Enlarged-strain-component in the tensile direction is the primary cause for higher plasticity in the high-carbon surface. Inhomogeneous fracture mode indicates the typical restraint of crack propagation in the core, suggesting greater toughness for the tempered CGSS.

Phase transformation and deformation behavior of a TiAl–Nb composite under quasi-static and dynamic loadings

To improve the high-temperature deformability of TiAl intermetallics, a TiAl–Nb intermetallic matrix composite was prepared by powder metallurgy to try to introduce the deformable β phase. The microstructure and deformation behavior of the TiAl–Nb intermetallic matrix composite under quasi-static and dynamic conditions were systematically investigated. It is found that the microstructure of the composite is composed of a near-gamma TiAl matrix and Nb-rich regions. In the Nb-rich regions a coexistence of βo, ωo and γ phases was identified where ωo and γ phases were supposed to directly precipitate in the βo matrix. The ultimate tensile strength of the composite exhibits different temperature-dependent behaviors under quasi-static and dynamic loading conditions. It increases with temperatures up to 650 °C and then declines with temperature under quasi-static loading, while it does not decrease from 650 to 850 °C under the dynamic loading. In the deformed microstructures, the Nb-rich regions at all conditions are still composed of βo, ωo and γ phases, indicating that the solvus temperature of the ωo phase could be above 850 °C. Additionally, the TiAl matrix appears to not significantly contribute to the plastic deformation of the composite, where the propensity of dislocations and mechanical twins do not significantly change when varying loading conditions. However, the γ particles formed in Nb-rich regions contain substantial mechanical twins and dislocations under both quasi-static and dynamic loading conditions. Thus, the γ particles directly transformed from the βo phase exhibit better deformability than the γ phase in the matrix. This could be probably explained by a decreased stacking fault energy for the newly formed γ phase due to a decrease in Al fraction and a significant increase in Nb fraction. Meanwhile, twin intersections occurred in the γ particles, and the induced stress concentration in the intersection regions was relieved by lattice distortion and detwinning processes. This twin intersection behavior could be beneficial for improving the composite strength without sacrificing much ductility.

Enhanced matrix precipitation of T1 (Al2CuLi) phase in AA2055 Al–Li alloy during stress aging process

Attempts to improve the strength of Gen3 Al–Li alloys without obviously deteriorating the ductility have been directed towards enhancing the matrix precipitation of T1 phase and reducing its enrichment at sub-grain boundaries. In this study, a novel artificial aging treatment during which uniaxial tensile stress was applied has been carried out on the AA2055 Al–Li alloy while a certain temperature was maintained. The microstructure, fractography, dislocation density, and the mechanical properties were analyzed by HAADF-STEM, HRTEM, DSC, SEM, FWHM of XRD patterns, and tensile tests. It was found that matrix T1 precipitation could be enhanced at the expense of θ’ phase by the stress applied. The enrichment of T1 phase at sub-grain boundaries could be observed in all specimens. However, the degree decreased as the pre-stretch and the applied external stress imposed. A good combination between strength and ductility was obtained for the specimen aged in T8SA100 temper (2% pre-stretch, 155 °C, 24 h, 100 MPa) and the average YS, UTS, and EI were 623 MPa, 649 MPa and 10.5%, respectively. The dislocation density in the stress aged specimens was higher than that in the stress-free aged specimens, indicating that the dislocation mechanism plays an important role in the enhanced T1 matrix precipitation during stress aging. The present study suggests that the novel stress aging treatment has great potential in improving the overall performance of advanced Al–Li alloys.

Phase decomposition in nanocrystalline Cr0.8Cu0.2 thin films

Metastable Cr0.8Cu0.2 alloy thin films with nominal thickness of 360 nm have been deposited on Si(100) substrate by co-evaporation of Cu and Cr using molecular beam epitaxy (MBE). Phase evolution, microstructure, stress development, and crystallographic texture in Cr0.8Cu0.2 thin films have been investigated by X-ray diffraction (XRD), atom probe tomography (APT) and transmission electron microscopy (TEM) combined with energy dispersive X-ray spectroscopy (EDS) during annealing of the films in the temperature range 200–450 °C. X-ray diffraction of the as-deposited thin film shows single phase bcc crystal structure of the film whereas APT observation of fine precipitates in the film matrix due to inherent compositional fluctuation indicates onset of phase separation via spinodal decomposition regime. XRD (in-situ) and APT investigation of 300 °C annealed film reveals that the early stage of phase separation involves localized formation of metastable intermediate bcc precipitate phase having 60 at% Cr and 40 at% Cu approximately (~Cr0.6Cu0.4). For longer duration of annealing at temperature ≥350 °C, such metastable bcc precipitates act as heterogeneous nucleation sites for the onset of precipitation of Cu rich fcc Cu(Cr) phase which indicates a change of phase separation mechanism from ‘spinodal decomposition’ to ‘nucleation and growth’. Annealing of the film at temperature ≥400 °C for longer duration leads to the formation of a two phase structure with Cu rich fcc precipitate phase in a Cr rich bcc matrix. Observed phase decomposition is accompanied by significant changes in the microstructure, residual stress and crystallographic texture in the Cr rich bcc film matrix which leads to the minimization of both surface and strain energies and thereby a reduction of total Gibbs free energy of the thin film. Thermodynamic model calculation has been presented in order to understand the nucleation pathway of Cu rich stable fcc Cu(Cr) precipitates via non-classical nucleation of metastable intermediate bcc Cr0.6Cu0.4 phase.

Non-Equilibrium Crystallization of Monotectic Zn-25%Bi Alloy under 600 g.

This study investigated the influence of supergravity on the segregation of components in the Zn–Bi monotectic system and consequently, the creation of an interface of the separation zone of both phases. The observation showed that near the separation boundary, in a very narrow area of the order of several hundred microns, all types of structures characteristic for the concentration range from 0 to 100% bismuth occurred. An additional effect of crystallization in high gravity is a high degree of structural order and an almost perfectly flat separation boundary. This is the case for both the zinc-rich zone and the bismuth-rich zone. Texture analysis revealed the existence of two privileged orientations in the zinc zone. Gravitational segregation also resulted in a strong rearrangement of the heavier bismuth to the outer end of the sample, leaving only very fine precipitates in the zinc region. For comparison, the results obtained for the crystallization under normal gravity are given. The effect of high orderliness of the structure was then absent. Despite segregation, a significant part of bismuth remained in the form of precipitates in the zinc matrix, and the separation border was shaped like a lens. The described method can be used for the production of massive bimaterials with a directed orientation of both components and a flat interface between them, such as thermo-generator elements or bimetallic electric cell parts, where the parameters (thickness) of the junction can be precisely defined at the manufacturing stage.

Microstructures and Mechanical Properties of Al-Ti-Zr-Nb-Ta-Mo-V Refractory High-Entropy Alloys with Coherent B2 Nanoprecipitation

In this work, the microstructural evolution and mechanical properties of new body-centered cubic (BCC)-based Al-Ti-Zr-Nb-Ta-Mo-V refractory high-entropy alloys (RHEAs) with coherent B2 precipitation are investigated. These designed alloy ingots were solid-solutionized at 1573 K for 2 h and then aged at 873 K for 24 h, in which each treatment was followed by water quenching. It was found that there exists phase separation of BCC matrix, Ti/Zr-rich BCC1 and Nb/Ta-rich BCC2 in these alloys. Moreover, ultra-fine spherical B2 nanoparticles with a size of 3~5 nm were dispersed in BCC2 matrix. These B2 nanoparticles could be coarsened up to 25~50 nm after aging and the particle morphology also changes to a cuboidal shape due to a moderate lattice misfit (ε = 0.7~2.0%). Also, Zr5Al3 phase could coexist with the B2 phase, where the difference between them is that the Ti element is enriched in B2 phase, rather than in Zr5Al3. Among them, the solutionized Al2Ti5Zr4Nb2.5Ta2.5 RHEAs exhibit good compressive mechanical property with a high yield strength of 1240 MPa and a large plasticity, which is mainly attributed to the coherent precipitation in the BCC matrix.

Fracture characteristics and heat treatment of laser powder bed fusion additively manufactured GRCop-84 copper

Laser Powder Bed Fusion (LPBF) of Glenn Research Copper 84 (GRCop-84), a Cr2Nb (8 at. % Cr, 4 at. % Nb) precipitation hardened alloy, produces a fully dense high conductivity alloy with a yield strength of 500 MPa and ultimate tensile strength (UTS) of 740 MPa, superior to other competing copper alloys, and 20% elongation at fracture for material stressed perpendicular to the build direction. The high thermal stability of the Cr2Nb precipitate in the copper matrix reduces coarsening and maintains a 300 MPa yield, 520 MPa UTS and 26% elongation after a 900 °C, 5-h heat treatment, while a 3 h 450 °C heat treatment increases yield to 810 MPa, UTS to 970 MPa with 9% elongation at fracture, for samples stressed perpendicular to the build direction. Tensile strength anisotropy based on print direction was attributed to internal stress and columnar grain formation. Void nucleation during tensile fracture was initiated by brittle fracture of precipitate particles within the copper matrix. Fracture cusps contain matching precipitate fragment geometry on opposing sides located near the cusp center in at least 80% of fracture cusps. An optimal precipitate size of 100 nm is predicted for maximum tensile strength from precipitates on fracture surfaces, while tensile testing with varying heat treatments shows maximum strength with 100 nm and smaller precipitates. Cr2Nb precipitates are shown to transition between polycrystalline and monocrystalline structures at high temperature.

Effect of rapid cooling after continuous heating on microstructure and mechanical properties of Zr50Cu34Al8Ag8 amorphous alloy

The effects of rapid cooling after continuous heating on mechanical properties and microstructure of Zr50Cu34Al8Ag8 amorphous alloy are investigated. The microstructure of the alloy is analyzed by X-ray diffraction, differential scanning calorimetry, scanning electron microscopy and transmission electron microscopy. Experimental results show that the rapid cooling of the amorphous alloy after heating to 450 °C possesses the best comprehensive mechanical properties, which can be attributed to the formation of 4.65% ordered crystal structures in the amorphous matrix. When the heating temperature rises to 480 °C, a large number of hexagonal Al2Zr and Ag2Al phases precipitate in the amorphous matrix, thereby deteriorating the alloy properties.

Design, phase equilibria, and coarsening kinetics of a new [formula omitted] precipitation-hardened multi-principal element alloy

Multi-principal element alloys (MPEAs), with dispersed nanometric precipitates in a ductile matrix, are attracting a considerable amount of literature’s attention. Understanding the coarsening kinetics and potential properties of such alloys is crucial for future developments in the field. In the present study, we report a new precipitation-hardened multi-principal element alloy, Cr29.7Co29.7Ni35.4Al4.0Ti1.2 (at%), developed with the aid of the CALPHAD method. The alloy has a tough Cr-Co-Ni FCC matrix and nanometric L12 precipitates. After standard heat treatments, the alloy was aged at 850 °C for different aging times and the coarsening kinetics was investigated. The evolution of mechanical properties as a function of aging time was evaluated through microhardness tests. An increment of 106 HV 0.5 was observed compared to the sample in the solution-treated condition. This hardness increment was higher than that of conventional superalloys with a similar volume fraction of precipitates. Experimental data indicate that particle growth during coarsening is governed by diffusion controlling mechanism. The coarsening rate constant was lower than that of traditional wrought superalloys aged at the same temperature, indicating better thermal stability of the current MPEA. Furthermore, experimental particle size distributions show a good correlation with the curve predicted by the Lifshitz–Slyozov–Wagner (LSW) theory. Deviations and the applicability of this theory for MPEAs are discussed.

Role of applied stress on the changes of precipitation and phosphorus segregation behavior in a TP347H austenitic stainless steel

The effect of applied stress on the precipitation (Nb-rich MC and Nb-rich M2P) behavior in the matrix and its role in the phosphorus segregation at the grain boundary (GB) are investigated in a TP347H austenitic stainless steel. The two parts (gage and grip) in the rupture test specimens under the applied stress of 80 MPa at 750 °C are investigated using TEM, SEM, and EPMA. Continuous precipitation and saturation behaviors of MC and M2P were observed in the grip part. Excess precipitation behavior of MC in the early stage of rupture test and the retarded precipitation of M2P were confirmed in the gage part. The retarded precipitation and the low volume fraction of M2P promoted phosphorus segregation at the GB. The correlation between the matrix precipitation and GB phosphorus segregation under the applied stress is further discussed.

Designing [formula omitted]-strengthened Al-Cr-Fe-Ni-Ti complex concentrated alloys for high temperature applications

For alloys with nanoprecipitate/matrix microstructures, the lattice coherency between the two phases plays an important role in determining the mechanical performances at high temperature. In this work, we systematically investigate the AlxCr13.3Fe71.5-xNi11.2Ti4 (x=8, 10, 12, 14, 16 at%) complex concentrated alloys with an aim to enhance the lattice coherency between the BCC matrix and L21 precipitate. The precipitate microstructures, lattice misfit and the resultant coherency strain evolution are comprehensively studied. With increasing Al from 8 at% to 16 at%, the interfacial structure gradually transforms from semicoherent to fully coherent interface by the decrease in precipitate size and lattice misfit, which leads to the stronger elastic interaction between the matrix and precipitate. Meanwhile, the crystal structure of precipitate is slightly distorted from cubic to tetragonal. The yield strength of alloys at room temperature continuously increases with the addition of Al by the solid-solution strengthening and precipitation hardening effect. Here, the mechanism of precipitation hardening changes from Orowan process to coherency strengthening. Interestingly, the strengthening effect by Al addition is further amplified in the tensile test at 700 °C. The higher degree of lattice coherency and the distorted structure of the precipitate resulting from the Al addition lead to the effective strain transfer and the stronger precipitate, respectively. Therefore, the Al16Cr13.3Fe55.5Ni11.2Ti4 alloy exhibits an excellent combination of yield strength (400.8 MPa) and ultimate tensile strength (572.9 MPa). These values are much higher than those of the previously reported nanoprecipiate-strengthened alloys, suggesting that the alloy is highly promising as high temperature structural applications.

Computational and Experimental Insights into the Role of Acidic Molecules on the Corrosion Behavior on 7A46 Aluminum Alloy.

The corrosion mechanisms for different corrosive media on the aged 7A46 aluminum alloy were systematically investigated at nanoscale level. The combination of empirical intergranular and exfoliation corrosion behavior was employed, and coupled with first-principles calculations. Results revealed that the dispersed distribution of matrix precipitates (MPs) leads to the enhancement of the corrosion resistance pre-ageing (PA) followed by double-ageing (PA-DA) alloy. The deepest corrosion depth of PA-DA alloy was in hydrochloric acid, and the calculation result demonstrates that the passivation effect in combination with the accumulation of corrosion products in nitric acid protect the PA-DA alloy from further corrosion.

Fatigue Crack Growth and Precipitation Characteristics of a High Zn-Containing Al-Zn-Mg-Cu Alloy with Various Typical Aging States

The fatigue crack growth of Al-Zn-Mg-Cu alloy can be adjusted by different aging treatments. In the present work, a high Zn-containing Al-Zn-Mg-Cu alloy was treated by single, double and triple stage aging treatments and typical T6, T79 and T77 states were selected by tensile properties. Fatigue crack growth under these aging states was tested and related fracture morphology and precipitation characteristics were observed. The results showed that fatigue crack growth resistance for the alloy was T6&lt;T79&lt;T77. The corresponding fracture morphology also showed the difference of fatigue striations and the measurement of them provided an additional evidence. The precipitation proved that the alloy with T6 state possessed GPI zone, GPII zone and η' phase while that for T76 state was GPII zone, η' phase and η phase. As for the T77 state, the precipitate types were GPII zone and η' phase. The matrix precipitate for T6 state was smaller and denser than that for T79 and T77 states while that for T77 state possessed a dense distribution than that for T79 state. The measurement of precipitate size distribution also proved it. The grain boundary precipitates for T79 and T77 states were similar, which had a more intermittent distribution than that for T6 state.

Influence of nanosized precipitate on the corrosion behavior of high-strength low-alloy steels: a review

Compared with the widely used plain carbon steels, high-strength low-alloy steels exhibit high tensile strength, excellent fatigue performance, good plasticity, and toughness, and have attracted considerable attention in recent years. In the strengthening and toughening of high-strength low-alloy steels, the addition of carbide-forming and nitride-forming elements (i.e., Nb, V, and Ti) promotes the formation of nanosized precipitates. Nanosized precipitate in high-strength low-alloy steels plays a significant role in the microstructure optimization, which could maintain the high mechanical properties and excellent corrosion resistance of the steel matrix. With the advancement of characterization techniques and simulation methods in the atomic scale over the past few decades, the effect of nanosized precipitate on the corrosion behavior of high-strength low-alloy steels has become increasingly clear. Based on the obtained achievements in China and abroad, the existing morphology of nanosized precipitate and its influence on hydrogen diffusion, uniform corrosion, stress corrosion cracking, and hydrogen-induced damage were reviewed systematically in this study. Results show that the influence of nanosized precipitates on the corrosion behavior of high-strength low-alloy steels depends on its size, quantity, and status of crystal deposition. The fine and (semi-)coherent precipitate in the steel matrix can significantly improve not only the corrosion resistance by refining the microstructure (including the substructure) but also the resistance to hydrogen-induced damage by acting as an irreversible hydrogen-trapping site and strongly restraining hydrogen diffusion. However, incoherent precipitates with a large size would deteriorate the corrosion resistance because of the loss of microstructure optimization. Finally, this study forecasts the influence of nanosized precipitate on fatigue corrosion of high-strength low-alloy steels, which has not been investigated in previous studies. The optimization of the corrosion resistance of high-strength low-alloy steels can be achieved by controlling the nanosized precipitates. Clarifying the influence of nanosized precipitate on corrosion behavior would contribute significantly to the development of high-quality high-strength low-alloy steels.