The martensite phases in 304 stainless steel

A detailed analysis of martensite transformations in 18/8 (304) stainless steel, utilizing transmission electron microscopy and diffraction in conjunction with X-ray and magnetization techniques, has established that the sequence of transformation is γ → ∈ → α. ε is a thermodynamically stable hcp phase whose formation is greatly enhanced as a result of plastic deformation. Comparison with the ε → α transformation in pure Fe-Mn alloys lends further support to the above sequence and suggests that a transformation line between ε and α in Fe-Cr-Ni alloys can be expected. In the 304 stainless steel used in this investigation, formation of α was induced only by plastic deformation and subsequent to formation of ε. Nucleation of α occurs heterogeneously at intersections of ε bands or where ε bands abut twin or grain boundaries (which represent unilaterally compressed regions). From electron diffraction, the Nishiyama relationship between γ and α phases appears to predominate at the start of the transformation, but then changes to that of Kurdjumov-Sachs. Based on these observations, a sequence of atom movements from the hcp structure to the bcc structure is proposed which has the basic geometric features of the martensitic transformation. Formerly with Department of Materials Science and Engineering, University of California, Berkeley, Calif.     

The sintering of 304L stainless steel powder

An examination of the shrinkage kinetics for a 304L stainless steel powder showed that initial densification is controlled by a strain assisted volume diffusion mechanism. At temperatures above 1330 K, grain growth reduces the shrinkage rate; however, at lower sintering temperatures, the shrinkage rate is temporarily increased by the proximity of the moving grain boundaries to the interparticle necks. The activation energies of volume diffusion (240±20 kJ/mol) and grain growth (285±35 kJ/mol) were in good agreement with prior results.     

The sintering of 304L stainless steel powder

An examination of the shrinkage kinetics for a 304L stainless steel powder showed that initial densification is controlled by a strain assisted volume diffusion mechanism. At temperatures above 1330 K, grain growth reduces the shrinkage rate; however, at lower sintering temperatures, the shrinkage rate is temporarily increased by the proximity of the moving grain boundaries to the interparticle necks. The activation energies of volume diffusion (240 ± 20 kJ/mol) and grain growth (285 ± 35 kJ/mol) were in good agreement with prior results.     

The erosion behavior of 304 stainless steel at elevated temperatures

The objective of this paper is to characterize the solid particle erosion behavior of an annealed 304 stainless steel (SS) over the temperature range of 300 to 763 K. Silicon carbide was used as the erodent. Impact velocity and angle were kept constant at 115 m/s and 90 deg (normal), respectively. The results indicated that the erosion rate of 304 SS as a function of test temperature went through a minimum at around 548 K. None of the empirical models or parameters proposed in the literature for correlating room-temperature erosion resistance with a variety of mechanical or thermophysical properties of the eroding or erodent material explained the observed erosion ratevs temperature behavior. However, the results were qualitatively explained on the basis of a localization model for erosion. An analysis of the erosion data also indicated that oxidation of the eroding material and related effects on erosion were unimportant even at the highest test temperature of 763 K.     

Research on martensitic transformation of 304 stainless steel

采用光学显微镜、扫描电镜、磁性测量和力学分析等手段,研究了304奥氏体不锈钢形变过程中发生开裂的原因,研究发现开裂是由于形变过程中发生了马氏体相变,导致塑性变差引起的,开裂处的磁性率达到了22.9%。发生马氏体转变的原因是由于w（Ni）低于标准下限,其组织稳定性下降,在形变过程中诱发了马氏体转变。     

Hydrogen assisted cracking of type 304 stainless steel

This paper reports a study of hydrogen assisted cracking in type 304 stainless steel. It shows that the most detrimental effect in increasing the susceptibility of the material to hydrogen cracking is the formation of martensite upon deformation. This is particularly damaging if the martensite is localized at the grain boundaries. With martensite present intergranular impurities such as phosphorus play a secondary role. As martensite becomes more difficult to form, the importance of impurities increases.     

Plastic flow phenomenology of 304L stainless steel

The isothermal plastic flow behavior of annealed 304L austenitic stainless steel in uniaxial compression and torsional modes of deformation has been established over a wide range of temperatures and strain rates. In uniaxial compression, it was found that high rates of strain hardening, which persist to large strains (?.7) at cold-working temperatures, are found only at small values of strain (?0.2) at hot-working temperatures because of the influence of dynamic softening processes. The effect of deformation heating on flow behavior, which occurs primarily at high strain rates, was most significant at cold-working temperatures. Deformation heating was observed to result in flow stress maxima and flow softening. A method of estimating high-strain rate, isothermal-flow curves in such instances was derived. Shear stress-shear strain curves derived from torsion tests exhibited dependences on temperature and strain rate similar to those observed in compression data. In contrast to the compression curves, however, the shear stress-shear strain curves showed lower rates of strain-hardening at room temperature, 400 °C, 800 °C, and (for high strain rates) 1000 °C. It was shown that the choice of definition for calculating effective stress-strain from the torsion data could not be modified to bring the two types of data into coincidence. Only a structure-sensitive explanation could be invoked to explain the difference.     

304不锈钢马氏体组织转变探讨

采用光学显微镜、扫描电镜、磁性测量和力学分析等手段,研究了304奥氏体不锈钢形变过程中发生开裂的原因,研究发现开裂是由于形变过程中发生了马氏体相变,导致塑性变差引起的,开裂处的磁性率达到了22.9%。发生马氏体转变的原因是由于w（Ni）低于标准下限,其组织稳定性下降,在形变过程中诱发了马氏体转变。     

The strain dependence of postdynamic recrystallization in 304 H stainless steel

Using double-hit hot compression tests, the softening behavior of 304 H stainless steel was studied during unloading. The prestrains used were associated with the initiation of dynamic recrystallization (DRX) (ε _c), the peak strain (ε _p), 1/2 (ε _c+ε _p), the strain at maximum softening rate (ε _i), and the onset of steady state flow (ε _s). The following conditions of deformation were used: T=1000 °C, 1050 °C, and 1100 °C, =0.01 and 0.1 s⁻¹, and delay times of 0.3 to 1000 seconds. To define the above important strains, single-hit hot compression tests were performed over a wider range of deformation conditions than the double-hit ones—i.e., 900 °C to 1100 °C and =0.01 to 1 s⁻¹. The results show that a transition strain (ε*) separates the strain-dependent range of postdynamic softening from the strain-independent range. At strains between ε _c and ε*, both metadynamic and static recrystallization contribute to interhit softening. The value of ε* obtained in this work was ε*=4/3 ε _p. It was also found that the strain hardening rate was identical at all the critical strains (ε*) and took the value −22 MPa.     

Intercrystalline structure distribution in alloy 304 stainless steel

The intercrystalline structure distribution function (ISDF) describes the probability density for the occurrence of grain boundaries in the polycrystalline medium with five specified geometrical parameters: three describing intercrystalline lattice misorientation and two describing the orientation of the grain boundary plane. This paper extends the ISDF analysis to Bunge’s formalism which represents the distribution in terms of a series expansion of symmetric generalized spherical harmonics. An exemplary calculation of the ISDF is illustrated for alloy 304 stainless steel tubing. The results confirm the observation that gS3 and gS9 boundaries, arising from twinning, are prevalent in the structure. The distribution of twinning boundaries and other special boundaries is represented by Euler plots in the five geometrical parameters defining boundary structure. One remarkable feature of this material is a nearly isotropic distribution of boundary misorientation in the two parameters defining the boundary plane orientation. These results are compared with other published experimental data and theoretical calculations for the distribution of special boundaries.     

Interpretation of high-temperature creep of type 304 stainless steel

The elevated-temperature creep behavior of Type 304 stainless steel is examined in terms of the measured effective and internal stresses. Results show that the mean effective stress is related to the applied stress by a power law of the form σ^* = α(σ)^β, where the constants α and β are functions of temperature. The dependence of creep rate on applied stress follows a power law, and the stress exponent is dependent on temperature. The latter behavior arises from the variation in the mean effective stress with applied stress and temperature. The creep rates are also described as a function of effective stress. The dislocation velocity-stress exponent obtained from stresschange tests is higher than the effective stress exponent evaluated from creep data. The dependence of creep rate on temperature at various values of effective stress yields a total activation energy of approximately the same magnitude as self-diffusion.     

304不锈钢热轧钢带边部质量控制

不锈钢热轧带钢边部是容易发生质量问题的敏感区域。介绍了304不锈钢在热轧钢带生产过程中易出现的边部鳞折、狭缝、粗糙痕迹等缺陷的主要形貌特征,分析了这些缺陷产生的原因。针对这些边部质量问题,并结合不锈钢生产经验,提出了一系列相应的改进方法和控制措施,对304不锈钢边部质量控制具有借鉴意义。     

Failure behavior of 304l stainless steel in torsion

The workability of 304L austenitic stainless steel has been investigated using torsion testing at temperatures from 20 °C to 1200 °C and strain rates of 0.01 and 10.0s ^-1 For the lower strain rate, temperature changes due to deformation heating were minimal, and failure was found to be fracture controlled at all temperatures. As for many other metals, the 304L exhibited a ductility minimum at warm-working temperatures. For the higher strain rate, failure was controlled by flow-localization processes at 20 °C and 200 °C. At these temperatures, flow softening resulting from deformation heating was deduced to be the principal cause of flow localization. A model to predict the strain at the onset of localization was developed and applied successfully to the 304L results. For high strain-rate torsion tests at 400 °C and above, failure was fracture controlled as in the low strain-rate tests, and the ductilities were shown to be correlated to those at the lower strain rate through the Zener-Hollomon parameter by employing an activation energy derived from flow-stress data.     

Prediction of fatigue crack formation in 304 stainless steel

Strain-controlled fatigue tests have been conducted on center-holed 304 stainless steel specimens. The fraction of total fatigue life spent until formation of an “engineering” crack ranged from about 15 to 85 pct, indicating the potential importance of being able to predict the fatigue crack formation life. A “just formed engineering crack,” as defined here, is a through crack long in the thickness direction, which has just emerged from the center hole. An energy based parameter, ΔσrΔε,, has been shown to correlate with the appearance of fatigue cracks in the center-holed 304 stainless steel specimens. This parameter is suggested to be more useful in predicting fatigue crack formation life than Δσ or Δε, alone. A good correlation was found over the limited range of data for two types of 304 stainless steel, a powder metallurgy (PM) stainless steel with higher than normal strength prop-erties and an ingot metallurgy (IM) stainless steel with normal strength properties. A better correlation was found for strain-controlled fatigue tests which did not go into compressive strain than for com-pletely reversed fatigue. Formerly a graduate student with the Materials Science and Engineering Department, Northwestern University, is     

304不锈钢熔体氮溶解度的测定

介绍并比较了纯铁液中氮溶解度测定方法--直接法和间接法,并在经典的间接法的基础上,重新设计了气体氮的配气、控制和计量系统,以及渗氮的方式.用该方法测定了304不锈钢熔体在不同温度和氮分压下的氮的溶解度值.     

Structure and properties of thermal-mechanically treated 304 stainless steel

Mechanical and thermal-mechanical treatments of 304 stainless steel enables yield strengths of over 200,000 psi to be obtained with elongations better than 10 pct. Electron microscopy, X-ray, and magnetic techniques show that during deformation, strain induced γ → ∈ → α transformation occurs with further thermal nucleation of α achieved by aging up to 400°C. The yield strength is linearly proportional to the amount of ° irrespective of the treatment used to form α. The yield strength is given by α_y = 225f + 48.65 ksi, where ƒ is the volume fraction of martensite. Softening occurs by aging at 500°C and above due to a decrease in percent α which may occur by renucleation of γ. The system is an unusual form of composite strengthening; hard martensite particles are formed within the austenite, and the percent α (and thereby the mechanical properties), can be controlled by the mechanical/thermal-mechanical processing. Formerly with the Department of Materials Science and Engineering, University of California, Berkeley, Calif.     

Inclusion and its deformation behavior in 304 stainless steel

Non-metallic inclusion is the main reason for the presence of surface defects in cold-rolled steel strip. In this study,the composition,morphology,and size of the non-metallic inclusion in hot-rolled 304 stainless steel strips are analyzed. Cold-rolled 304 stainless steel strips with different cold-rolling reduction have been prepared,and the morphology and size of inclusion in these cold-rolled strips are also analyzed. Furthermore,the deformation behavior of a non-metallic inclusion during the cold-rolling process is studied. The results showthat Ca O-SiO2-MgO-Al2O3,a kind of brittle compound oxide,is the main type of inclusion in hot-rolled 304 stainless steel strips.During the cold-rolling process,ductile deformation of this type of inclusion is not obvious,where large inclusions are crushed,and the average size of inclusions in cold-rolled strips decreased while the cold-rolling reduction increased.     

Differences in oxides on large-and small-grained 304 stainless steel

The oxides formed on large-grained (∼40 °m) and small-grained (∼4 μm) 304 stainless steel oxidized in air at 800 °C have been examined and compared by Auger electron spectroscopy to learn more about the role of grain boundaries in the oxidation of the materials. For vacuum preannealed specimens, relatively thick iron oxides formed over the grains and thin, chromium-rich oxides formed over grain boudaries of large-grained material. The oxide formed over the entire surface of the small-grained material was a thin chromium-rich layer similar to that formed over grain boundaries of the large-grained samples. The oxidation of both small- and large-grained samples was consistent with selective formation of Cr₂O₃ at grain boundaries followed by a lateral diffusion of Cr and spreading of Cr₂O₃. A protective Cr₂O₃ layer formed readily on small-grained material but not on large-grained material. In contrast to the differences in oxide morphology for small- and large-grained preannealed specimens, oxide morphologies were similar for small- and large-grained material when the outer surface layer was removed by polishing after annealing and before oxidation tests. Surface differences, not adequately defined by Auger and SEM studies, caused marked changes in oxide morphologies for large-grained material. The difference in oxidation behavior before and after polishing was attributed to enhanced oxidation at grain boundaries during the vacuum preannealing treatment and to differences in defect concentrations in the surface region.