310S Austenitic Stainless Steel Research Articles

Microstructure and mechanical properties evolution of 310S and GH3536 in hydrogen metallurgy service

The evolution of microstructure and mechanical properties of 310S austenitic stainless steel and GH3536 nickel-based alloy in hydrogen metallurgy service condition is investigated by conducting heat treatment under high temperature and hydrogen atmosphere. As the annealing time increases at 750 °C, carbide precipitate phases of the σ and μ brittle phases appear in the materials. At 900 °C, the dissolution of carbides induces the dispersion of brittle phases, while the hydrogen content reaching its peak. These brittle phases are still present at defects like grain boundaries at 1050 °C, with the surface of precipitates showing corrosion pits. Materials exhibit increasing strength and hardness initially with temperature and annealing time, followed by a decrease. Meanwhile, fracture elongation shows a positive correlation with temperature but a negative correlation with time. After annealing at 1050 °C for 500 h, GH3536 retains its high-temperature softening behavior and elongation at fracture, demonstrating excellent plastic stability. Furthermore, the mechanism of high temperature and hydrogen affecting metals is expounded, providing reference for the selection and optimization of materials which service in high temperature and hydrogen.

Enhancement of hydrogen embrittlement resistance in 310S austenitic stainless steel through ribbon-like δ-ferrite

In general, δ-ferrite phases, especially in the weld, are not conducive to the hydrogen embrittlement (HE) resistance of austenitic stainless steels (ASSs). However, it is interesting to note that if a ribbon-like δ-ferrite was introduced into ASS, its HE resistance can be improved. In this work, we take 310 S ASS as an example and form a ribbon-like δ-ferrite on the original austenite grain boundary by quenching at 1200℃. This newly formed ribbon-like δ-ferrite phase not only alters the hydrogen enrichment characteristic from austenite grain boundaries to austenite/δ-ferrite interfaces but also contributes to an increased resistance to HE.

The effect of different surface treatments of 310S austenitic stainless steel on the corrosion behavior in supercritical water using slow positron methods

AbstractThe corrosion behavior of 310S austenitic stainless steel, subjected to different surface treatments machined (MA), sandblasting (SB), and polishing (PO), was exposed to a 550°C supercritical water (SCW) environment. The aged samples were analyzed using variable‐energy slow positron beam techniques. The obtained results revealed that the plastic deformation of the near‐surface region of the MA and SB samples was substantially recovered in the SCW conditions. At least two distinct oxide layers formed, and the oxidation process created a Fe/Cr depletion zone in the inner layer. Various surface treatments, however, led to different corrosion profiles. The depth profile of slow positron beam characterization suggests that significant residual stress and deformation zones on the surfaces of the sandblasted samples probably provided a diffusion path for the oxidation of the 310S. Only the SB samples exhibited a negative weight change after SCW exposure. At the same time, the SB samples showed the highest concentration of the positron traps in this region, which was explained by open‐volume defects associated with the microcracks introduced by sandblasting.

Orthogonal turning of AISI 310S austenitic stainless steel under hybrid nanofluid-assisted MQL and a sustainability optimization using NSGA-II and TOPSIS

AISI 310S austenitic stainless steels are widely used in many industries, such as oil, gas, and petrochemical industries containing hot concentrated acids, due to their superior properties like corrosion resistance, high-temperature service, and creep resistance. However, a study on the machining of AISI 310 stainless steel has not been published in the scientific literature. It is known that the machinability of the austenitic stainless steel alloys, in which the AISI 310S alloy is included, is poor due to its low thermal conductivity, high work hardening, and built-up edge (BUE) formation. This situation causes sustainability problems by increasing the energy consumptions, the total machining cost and the amount of carbon emissions. The presented study investigated for the first time machining response and sustainability assessment in the orthogonal turning of AISI 310S stainless steel using three different cutting speeds and feed values, and five different cutting conditions such as dry, vegetable-based fluid minimum quantity lubrication (MQL), nano molybdenum disulfide (nMoS2) reinforced nanofluid MQL, nanographene (nGP) reinforced nanofluid MQL, and nMoS2/nGP reinforced hybrid nanofluid MQL, and a sustainability optimization was performed. Sustainability optimization was conducted to minimize the resultant force, surface roughness, carbon emission, and total machining cost using multi-objective optimization with NSGA-II (Non-dominated Sorting Genetic Algorithm II) and multi-criteria decision-making with TOPSIS (Technique for Order of Preference by Similarity to Ideal Solution). The resultant force, surface roughness, total carbon emission, and total machining cost were reduced by a significant, 56.8%, 86.8%, 30.4%, and 2.9%, respectively, under the nGP reinforced nanofluid MQL cutting condition compared to the dry cutting condition. As a result of sustainability optimization, the use of high cutting speed (220 m/min), low feed values (between 0.11 mm/rev and 0.14 mm/rev), and nGP reinforced nanofluid MQL method (N2-MQL) in the turning of AISI 310S stainless steel material provides the optimum surface roughness values, cutting forces, carbon emissions, and total machining costs.

Microstructure and texture evolutions of 310S austenitic stainless steel after cryogenic rolling and subsequent annealing: X-ray and electron backscatter diffraction studies

Microstructure and texture evolutions of 310S austenitic stainless steel after cryogenic rolling and subsequent annealing: X-ray and electron backscatter diffraction studies

Effects of nano-ceramic additives on high-temperature mechanical properties and corrosion behavior of 310S austenitic stainless steel

Effects of nano-ceramic additives on high-temperature mechanical properties and corrosion behavior of 310S austenitic stainless steel

Effect of sulfur, phosphorus, silicon, and delta ferrite on weld solidification cracking of AISI 310S austenitic stainless steel

Solidification cracking is very common in the welding process of austenitic stainless steels and can lead to premature failures. Yet, the main quantitative impact of S, P and Si on solidification cracking is still lacking. In addition, the present solidification cracking prediction diagrams are merely composition based, i.e., Creq/Nieq dependent. Hence, this work aim to highlight the importance of controlling S, P, Si, and δ-ferrite on the susceptibility of AISI 310S to solidification cracking. Penetrant testing, XRF spectrometry, hardness, ferrite measurements, along with microscopic examination were used. XRF spectroscopy revealed 0.09% S, 0.09% P and 2.27% Si at the weld which are deemed to be in critical range according to the reported literature and ASTM A240. Benchmarking the results with the modified Suutala and Pacary curves revealed close results. Therefore, outcomes from this work can aid in the development of such prediction diagrams, along with improvement to the refining industry.

Investigation of The Effects of Temperature on Physical, Mechanical And Electrical Conductivity Properties in AISI 310S Austenitic Stainless Steel

In our study, annealing was done to AISI 310S stainless steel at 800 °C. The effects of these annealing on structural, morphological, mechanical and electrical conductivities were investigated. From XRD results, it has been observed that the material is austenite and cubic in nature. SEM analysis has shown that the surface of AISI 310S steel changes with temperature. The tensile test of the material was made and it was observed that the tensile strength of the material decreased with the effect of temperature. In addition, the conductivity behavior of AISI 310S steel was measured with four probe technique depending on heat treatment. As a result of the measurements, it was observed that the resistance value increased and the conductivity value decreased in the heat treated material.

In situ observation of solidification crack propagation for type 310S and 316L stainless steels during TIG welding using synchrotron X-ray imaging

In situ observation of solidification cracking at the weld bead during tungsten inert gas (TIG) welding for type 310S and 316L austenitic stainless steels without the application of an external force was carried out using synchrotron X-ray radiography. The temperature distribution at the weld bead was simultaneously measured using a high-speed camera to directly determine the temperature, in which the propagation of solidification cracking occurred. The solidification cracking was clearly identified and it continuously propagated in the welding direction. The interface of the solidification cracking showed an irregular and zigzag morphology. It was found that the tip velocity of the solidification cracking periodically changed by translating between the high solid fraction (~ 90%) and the relatively lower solid fraction (~ 70%) regions at the centerline of the weld bead for both the type 310S and 316L stainless steels. The solidification cracking propagated at the lower temperature than the solidus temperature due to the segregation of low melting-point components. The tensile strain and strain rate were highly localized in the propagated area every 0.1 s which was the almost same as the time period, in which the tip velocity of the solidification cracking remarkably increased. The periodicity of the solidification cracking velocity at the weld bead can be explained by the dendrite morphology at each solid fraction and strain rate.

Dissimilar Welding Between 1.4742 Ferritic and 310S Austenitic Stainless Steels: Assessment of Oxidation Behaviour

In the present work, the isothermal and cyclic oxidation behaviour of the 1.4742 ferritic and 310S austenitic stainless steels together with their dissimilar metal welds was investigated in the air with the humidity of 30 ± 3%. The welding was performed by the gas tungsten arc welding process utilizing ER310, ERNiCr-3, and ER446 filler metals. In the isothermal conditions, all the tested specimens followed the parabolic rate law. The maximum and minimum kp values were related to the 310S-BM, 1.89 × 10−1 mg2 cm−4 h−1, and the 1.4742-BM, 0.03 × 10−2 mg2 cm−4 h−1, respectively. Due to the formation of a dense and thin mono-layer of Cr–Fe–Al spinel ((Cr,Fe,Al)3O4) on the surface of the 1.4742 stainless steel alongside the lowest coefficients of the thermal expansion (CTE), it exhibits a highly satisfying oxidation resistance in both isothermal and cyclic conditions. In the cyclic conditions, except for the 1.4742-BM, the other specimens encountered the oxide scale cracking and spallation. The large CTE mismatch between the underlying 310S-BM, -BMS, and ER310-WM with the multi-layer chromia (Cr2O3) and Cr–Mn spinel ((Cr,Mn)3O4) oxide scale caused extensive spallation and mass loss in cyclic conditions. The ERNiCr-3-W in comparison with the two other weldments, by reducing the thermal expansion mismatch between the adjacent underlying metals and the better oxidation resistance of the nickel-base ERNiCr-3-WM, showed better oxidation resistance in both isothermal and cyclic conditions.

On the Dissimilar Metal Welding of 1.4742 Ferritic to 310S Austenitic Stainless Steels Utilizing Different Filler Metals

In this work, the microstructural, mechanical, and physical properties of dissimilar welding between the 1.4742 ferritic and 310S austenitic stainless steels have been investigated. The welding was performed by the manual gas tungsten arc welding process utilizing ER310, ERNiCr-3, and ER446 filler metals. The weld metal microstructure of the ER310 and ERNiCr-3 filler metals was fully austenitic. The ER446 weld metal exhibited a ferritic-austenitic dual-phase microstructure. Carbide precipitates enriched with Cr, Fe, and or Nb were detected in all of the three weld metals. The unmixed zone was observed on both sides of the ERNiCr-3 weld metal, while for the ER310 and ER446 weld metals it was formed solely on one side. The ER446 weld metal displayed the maximum hardness values, 221.9 ± 5 HV, with relatively large fluctuations. The highest and lowest impact energy was achieved in the ERNiCr-3 weld metal, 40 ± 3 J, and ER446 weld metal, 25 ± 3 J, respectively. The ERNiCr-3 weld metal had a linear coefficient of thermal expansion (CTE) value about the mean value of the linear CTE of the two base metals. At last, for the dissimilar welding of these two base metals, it was concluded that the ERNiCr-3 filler metal is a better selection.

Microstructural Characterization and Mechanical Properties of TIG-Welded API 5L X60 HSLA Steel and AISI 310S Stainless Steel Dissimilar Joints

Dissimilar joining of API 5L X60 ferritic HSLA steel and AISI 310S austenitic stainless steel was conducted by tungsten inert gas (TIG) welding process using ERNiCr-3, ER310, ER2209, and ER309L filler metals. Microstructural characteristics and mechanical properties of the weldments were studied using optical and scanning electron microscopy, ferritometry, microhardness, tensile, and impact tests. The microstructure investigations revealed macro-segregation occurrence and formation of Type II boundaries at the interface of welds with API 5L X60 steel. In tension tests, the joints prepared by ER2209 filler metal showed the maximum yield and ultimate tensile strength values, and the failures were always obtained at the side of API 5L X60. The results of Charpy impact tests indicated that the maximum fracture energy is related to the weld made by ER2209 filler metal. At last, it was concluded that for the dissimilar welding between API 5L X60 and AISI 310S, the weld metal prepared by ER2209 duplex stainless steel filler metal offers the optimum properties at room temperature.

Correlation between Fatigue Crack Growth Behavior and Fracture Surface Roughness on Cold-Rolled Austenitic Stainless Steels in Gaseous Hydrogen

Austenitic stainless steels are often considered candidate materials for use in hydrogen-containing environments because of their low hydrogen embrittlement susceptibility. In this study, the fatigue crack growth behavior of the solution-annealed and cold-rolled 301, 304L, and 310S austenitic stainless steels was characterized in 0.2 MPa gaseous hydrogen to evaluate the hydrogen-assisted fatigue crack growth and correlate the fatigue crack growth rates with the fracture feature or fracture surface roughness. Regardless of the testing conditions, higher fracture surface roughness could be obtained in a higher stress intensity factor (∆K) range and for the counterpart cold-rolled specimen in hydrogen. The accelerated fatigue crack growth of 301 and 304L in hydrogen was accompanied by high fracture surface roughness and was associated with strain-induced martensitic transformation in the plastic zone ahead of the fatigue crack tip.

Corrosion of 310S Austenitic Stainless Steel in Simulated Rocket Combustion Gas

High temperature corrosion of 310S austenitic stainless steel in simulated rocket combustion gas at 900 degree Celsius was investigated and discussed in this paper. 310S austenitic stainless steel was chosen because it was used for building some components of a rocket launcher. The corrosive atmosphere was prepared by mixing of hydrochloric acid and distilled water with 5.5 mole per liter then, boiling that solution and feeding into a corrosion testing chamber. The chamber was set up at 900 degree Celsius with duration 210 hrs. After testing, the corroded specimen was microscopically characterized by OM and SEM/EDS techniques. The corrosion layer was classified into three main sublayers: peeling-off scale, external corrosion sublayer, and internal corrosion sublayer. The local chemical information was analyzed by XRD (in case of peeling-off scale) and SEM/EDS (in case of external and internal corrosion sublayers). The peeling off scale mainly comprised Fe2O3 and Fe21.3O32 ferrous oxides because they needed much oxygen consumption to exist. In case of external and internal sublayers, there were a lot of pore tunnels and corrosion products. Chlorine and/or hydrogen chloride would penetrate through a passive film and, then, metal chlorides was formed on both external and internal corrosion sublayers. Metal chlorides would volatile because of their lower evaporation temperature than the testing temperature. Moreover, they were oxidized by oxygen in wet condition and resulted metal oxides mostly remaining on the external corrosion sublayer.

Stress Corrosion Cracking Behaviour of Dissimilar Welding of AISI 310S Austenitic Stainless Steel to 2304 Duplex Stainless Steel

The influence of the weld metal chemistry on the stress corrosion cracking (SCC) susceptibility of dissimilar weldments between 310S austenitic stainless steel and 2304 duplex steels was investigated by constant load tests and microstructural examination. Two filler metals (E309L and E2209) were used to produce fusion zones of different chemical compositions. The SCC results showed that the heat affected zone (HAZ) on the 2304 base metal side of the weldments was the most susceptible region to SCC for both filler metals tested. The SCC results also showed that the weldments with 2209 duplex steel filler metal presented the best SCC resistance when compared to the weldments with E309L filler metal. The lower SCC resistance of the dissimilar joint with 309L austenitic steel filler metal may be attributed to (1) the presence of brittle chi/sigma phase in the HAZ on the 2304 base metal, which produced SC cracks in this region and (2) the presence of a semi-continuous delta-ferrite network in the fusion zone which favored the nucleation and propagation of SC cracks from the fusion zone to HAZ of the 2304 stainless steel. Thus, the SC cracks from the fusion zone associated with the SC cracks of 2304 HAZ decreased considerably the time-of-fracture on this region, where the fracture occurred. Although the dissimilar weldment with E2209 filler metal also presented SC cracks in the HAZ on the 2304 side, it did not present the delta ferrite network in the fusion zone due to its chemical composition. Fractography analyses showed that the mixed fracture mode was predominant for both filler metals used.

Corrosion resistance of 310S and 316L austenitic stainless steel in a quaternary molten salt for concentrating solar power

This paper evaluates the corrosion of 310S and 316L austenitic stainless steel in a quaternary molten salt KNO3-NaNO2-NaNO3-KCl (wt%, 50.35:38:6.65:5) at 500℃. The corrosion rates were determined using gravimetric analysis, which measures the weight loss over 1848h in order to identify the corrosion products with field-emission scanning electron microscope (FESEM) and X-ray diffraction (XRD).The results showed that the corrosion rate of these two austenitic stainless steels has the highest value at the initial stage, and then decrease followed by a constant value, which is due to the formation of protective oxide film on the interface to prevent further corrosion. Compared to 316L, 310S has better corrosion-resistance in the salt, since it contains more Cr and Ni element. The corrosion layer thickness of the 310S and 316L is 1.613μm and 2.903μm based on the cross-section micrographs, which is equal to 0.499μm/year and 1.460μm/year, respectively.

Influences of Mo/Zr minor-alloying on the phase precipitation behavior in modified 310S austenitic stainless steels at high temperatures

High-Cr/Ni austenitic stainless steels (ASSs) have attracted more attention as fuel cladding materials of super-critical water reactors due to their excellent comprehensive properties. In order to further improve their microstructural stability at high temperatures, the present work investigated systematically the influences of Mo/Zr contents and Zr/C ratios on the phase precipitation behaviors and mechanical properties of modified 310S ASSs. The designed alloy ingots were hot-rolled, solid-solutioned at 1423K for 0.5h, stabilized at 1173K for 0.5h, and then aged at 973K for different hours. The microstructure and precipitated phases at different heat-treatment states were characterized with OM, SEM, EPMA and TEM, respectively. All the results indicated that the excess addition of Mo and Zr and the inappropriate Zr/C ratios would promote the formation of Cr23C6, G-Ni16Si7Zr6 and (Ni,Fe)23Zr6 phases, resulting in the σ phase precipitation at the early stabilization stage. Furthermore, the formation mechanism of σ phase was discussed. The effects of the precipitated phases on the mechanical properties of alloys were then studied. It was found that the Fe-22Ni-25Cr-0.046C-0.37Mo-0.35Zr (wt%) alloy with appropriate Mo content and Zr/C ratio of 1/1 exhibits the best microstructural stability and good tensile mechanical property, in which only a few σ particles are precipitated from the matrix even after aging at 973K for 408h.

Isothermal and Cyclic Aging of 310S Austenitic Stainless Steel

Unusual damage and high creep strain rates have been observed on components made of 310S stainless steel subjected to thermal cycles between room temperature and 1143 K (870 °C). Microstructural characterization of such components after service evidenced high contents in sigma phase which formed first from δ-ferrite and then from γ-austenite. To get some insight into this microstructural evolution, isothermal and cyclic aging of 310S stainless steel has been studied experimentally and discussed on the basis of numerical simulations. The higher contents of sigma phase observed after cyclic agings than after isothermal treatments are clearly associated with nucleation triggered by thermal cycling.

Pulsed current and dual pulse gas metal arc welding of grade AISI: 310S austenitic stainless steel

Abstract The transverse shrinkage, mechanical and metallurgical properties of AISI: 310S ASS weld joints prepared by P-GMAW and DP-GMAW processes were investigated. It was observed that the use of the DP-GMAW process improves the aforementioned characteristics in comparison to that of the P-GMAW process. The enhanced quality of weld joints obtained with DP-GMAW process is primarily due to the combined effect of pulsed current and thermal pulsation (low frequency pulse). During the thermal pulsation period, there is a fluctuation of wire feed rate, which results in the further increase in welding current and the decrease in arc voltage. Because of this synchronization between welding current and arc voltage during the period of low frequency pulse, the DP-GMAW deposit introduces comparatively more thermal shock compared to the P-GMAW deposit, thereby reducing the heat input and improves the properties of weld joints.

Evaluation of solidification cracking susceptibility of Fe–18Mn–0·6C steel welds

Solidification cracking susceptibilities of high Mn steel welds were evaluated in the present study. A longitudinal Varestraint technique was utilised to assess the solidification cracking behaviours of the fusion zone. High Mn steel welds were more susceptible to solidification cracking than 304 and 202 austenitic stainless steel welds, however, they were less susceptible than 310S austenitic stainless steel welds. Extensive segregations of Mn and C took place at the dendritic and grain boundaries in the weld metal, and accordingly contributed to the increase of the hot cracking susceptibility of high Mn steel by the enlargement of solidification temperature range. Further, continuous γ-(Fe,Mn)3C eutectic phases formed at 1090°C along the grain boundary primarily resulted in the increase of solidification cracking sensitivity in high Mn steel.