Effects of Unloading on Subsequent Yielding Behavior in 304 Stainless Steel

1 Introduction

As multi-phase, complex microstructures are increasingly used to achieve strength and ductility targets, the deformation response of advanced high strength steels becomes more complicated and may deviate from expected with respect to temperature (Tsuchida et al., 2011; Coryell et al., 2013), strain rate (Zou et al., 2017), and strain state (Zou et al., 2018). Further, complex operations often involve varying strain states, strain rates, friction conditions, temperatures, and multiple, non-linear deformation steps. The newest generation of advanced high strength steels are increasingly difficult to form, because the higher strength requires presses with higher tonnages, and decreased ductility may cause the part to fail during a forming operation (Billur and Altan, 2012).

The yielding response of metals has been defined using criteria, such as the Hill (1948), Tresca (1864), or Mises (1913), that allow engineers to predict when a material will yield based on the stress state. These criteria focus largely on material that has not experienced straining in various directions prior to deformation. The criteria for yielding have been adapted for the Bauschinger effect and changing the strain path of the test (Naghdi et al., 1957; Holmedal, 2019) showing that prior deformation will change the shape and location of the yield surface. The presence of path-dependent yield behavior requires an in-depth analysis of the yield surface to be used in operations in which material undergoes multiple stages of deformation. This is further complicated by yielding behavior tied to experimental variables, such as testing temperature and strain rate.

In experiments done by Mendiguren et al., the loading/unloading mechanical behavior was observed for a TRIP700 steel (Mendiguren et al., 2015). During testing, an upper yield point was observed and explained by strain aging and the Snoek phenomenon, which is the stress induced redistribution of interstitial atoms in a body centered cubic lattice. Similar yielding behavior was also observed by Rathbun et al. and Lichtenfeld et al. in metastable austenitic stainless steels, which was explained by strain aging (Rathbun et al., 2000) and adiabatic heating of the samples (Lichtenfeld et al., 2006). Haasen and Kelly also observed this behavior in face centered cubic materials, and explained the phenomena by the pinning and unpinning of dislocations at short range barriers in the microstructure (Haasen and Kelly, 1957).

304 stainless-steel is a metastable austenitic stainless-steel; during deformation the austenite may transform to martensite due to a deformation induced transformation. This transformation is characterized by the TRansformation Induced Plasticity (TRIP) effect, which is known to increase the work hardening rate while accommodating strain thereby, delaying necking and improving the strength and ductility. TRIP is influenced by many factors, including the imposed strain state, as well as the direction of straining (Streicher et al., 2002; Alturk et al., 2018; Zou et al., 2018). In a study done by Streicher et al., a TRIP780 steel exhibited differing amounts of retained austenite transformation during straining in different strain states relative to the rolling direction, showing an increase in amount of martensite formed as a function of strain (Streicher et al., 2002). In a recent study by Finfrock et al., the amount of retained austenite transformation was dependent on the strain state relative to the rolling direction (Finfrock et al., 2020). The amount of transformation from austenite to martensite has also been shown to be dependent on strain state in 304 stainless-steel, with biaxial tension transforming more austenite than uniaxial tension (Hecker et al., 1982).

2 Materials and Methods

A 0.90 mm sheet of 304 stainless-steel that was cold rolled and fully annealed to develop a fully austenitic equiaxed microstructure with an average austenite grain size of 13 μm (Lewis, 1999). The 304 stainless-steel was waterjet cut into ASTM E8 subsize tensile specimens with a 25.4 mm gauge length. The composition of the steel is given in Table 1.

TABLE 1

TABLE 1. Composition of the 304 stainless-steel sheet, Wt.%.

Specimens were removed from both the rolling direction (RD) and transverse direction (TD). After cutting, samples were used for interrupted tensile testing. The interrupted testing consisted of deforming the sample in tension at a strain rate of 0.001 s⁻¹ on an MTS^® Alliance^® 20 kip uniaxial electromechanical load frame. Two samples were pulled to failure in both the TD and RD to establish baseline properties. Additional samples from each direction were used for interrupted tensile testing. Interrupted tests were performed with incremental cross-head displacements of nominally 1.5 mm (3 pct strain) below 15 pct total strain, and 3 mm (7 pct strain) above 15 pct total strain. Samples were then either unloaded and removed from the frame for a room temperature isothermal hold, unloaded and immediately reloaded to start the next straining increment, or unloaded partially and immediately reloaded to the next straining increment.

3 Results

The 304 stainless steel exhibited a difference in monotonic tensile properties along the RD and TD, as shown in the true stress-true strain and instantaneous strain hardening exponent (n_i) plots presented in Figure 1. The instantaneous strain hardening rate was evaluated until the onset of necking using Equation 1 (Dieter, 1976)

$n_i=\frac{\partial ln\left(\sigma \right)}{\partial ln\left(\mathit{ϵ}\right)}(1)$

where σ is the true stress and ϵ is the true strain. The instantaneous strain hardening rate increasing with strain indicates the TRIP effect active. After establishing the properties of the steel under monotonic loading, one sample in each direction was interrupted during tensile testing at various strains.

FIGURE 1

FIGURE 1. Baseline mechanical properties of a 304 stainless-steel in the rolling (RD) and transverse (TD) directions of the sheet with instantaneous strain hardening exponent (n_i) plotted to the onset of necking. The mechanical properties of the steel vary with orientation relative to the rolling direction, and there is significant strain hardening in the samples due to the TRIP effect.

Figure 2 shows the engineering stress vs. strain results of the samples interrupted in the RD (Figure 2A) and TD (Figure 2B) with respect to the baseline mechanical properties. For the interrupted tests, a yield point begins to develop with increasing strain. This behavior is characterized by an initially higher yield stress, followed by a constant or negative strain hardening rate, and then finally a return to the flow behavior associated with the monotonically loaded sample. The change in stress was measured as the difference between the stress value observed during reloading and the value that is observed at the same total strain in a monotonic test.

FIGURE 2

FIGURE 2. Engineering stress vs engineering strain of a 304 stainless-steel in the (A) rolling direction and (B) transverse direction from monotonic and interrupted tests. Tests were performed at room temperature and a strain rate of 0.001 s⁻¹. The interrupted tests were fully unloaded and held at room temperature prior to reloading.

The difference in yielding behavior is defined as $\text{Δ}\sigma$ , which is plotted with respect to the strain for the RD and TD samples with a room temperature hold for 2 h, with the exception of the hold at approximately 0.7 strain which was performed for much greater than 2 h (Figure 3). The calculation of $\text{Δ}\sigma$ is done by taking the difference in upper yield point and the engineering stress value at that strain using the work hardening behavior exhibited by the sample. This is shown schematically in Figure 4.

FIGURE 3

FIGURE 3. Change in yielding ($\text{Δ}\sigma$) after an isothermal 2 h hold at room temperature of a 304 stainless steel in the rolling direction and transverse direction during interrupted tensile tests performed at room temperature and a strain rate of 0.001 s⁻¹. The maximum seen at a strain of ∼0.7 strain corresponds to an extended isothermal hold at room temperature.

FIGURE 4

FIGURE 4. Change in yielding ($\text{Δ}\sigma$), shown as the difference between the upper yield point and the stress at the strain of the maximum yield assuming the work hardening rate of the sample after yielding.

This calculation was also performed for the samples that were fully unloaded with no hold time before reloading (Figure 5), and samples that were partially unloaded (45 kg, less than 2 pct of the max load) and immediately reloaded with no isothermal room temperature hold (Figure 6).

FIGURE 5

FIGURE 5. Change in yielding of a 304 stainless steel during interrupted tensile testing performed at room temperature and a strain rate of 0.001 s⁻¹, with and without an isothermal hold between straining steps.

FIGURE 6

FIGURE 6. Change in yielding of a 304 stainless steel during interrupted tensile testing performed at room temperature and a strain rate of 0.001 s⁻¹, with a full unload and partial unload between straining steps without an isothermal hold at room temperature.

4 Discussion

The 304 stainless-steel exhibited similar mechanical properties when subjected to interrupted straining, demonstrating strength and ductility levels equivalent to the properties when tested monotonically, with the exception of the yield point that occurred during some interrupted tests.

Interrupted straining showed that a yield point developed as strain increased, and increased in magnitude as strain increased. This yield point was similar to the phenomena reported by Haasen et al. during interrupted testing of pure single crystal face center cubic aluminum and nickel (Haasen and Kelly, 1957). Likewise, yield points bore resemblance to those presented by Rathbun et al. and Lichtenfeld et al. for 301, 302 (Rathbun et al., 2000), and 304 (Lichtenfeld et al., 2006) stainless steel. Rathbun et al. indicated that strain aging occurred at ambient temperature in 301 and 302 stainless steels and exhibited similar behaviors during straining, however strain aging was only present when deformation induced martensite existed in the microstructure (Rathbun et al., 2000). Lichtenfeld et al. attributed the yield point phenomena seen in 304 stainless steels at strain rates of 0.125 s⁻¹ and 1.25 × 10⁻⁴ s⁻¹ to a testing artifact (Lichtenfeld et al., 2006), and indicated that the actuator used for testing applied an anomalously high strain rate for a short period of time, which caused a temporary loss in the closed loop control, resulting in an artificially high strain rate, and therefore yield stress. The authors also claimed that strain aging did not occur; rather, any potential yield points were attributed to the thermal softening of austenite due to deformation induced heating, causing the yield stress to be higher upon reloading than it would be in a monotonic test in which heat was not dissipated (Lichtenfeld et al., 2006). In this study, the samples that were reloaded immediately at a rate of 0.001 s⁻¹ exhibited a yield point which was comparable to the yield points of samples that were held at room temperature. This suggest that thermal softening due to specimen heating was not a valid explaination for the yield points observed here. This temperature increase is negligible, therefore the samples likely did not see significant heating during straining. It should be noted that the samples immediately reloaded exhibited $\text{Δ}\sigma$ values that are smaller in magnitude to the samples that were held at room temperature. This is consistent with the results seen by Haasen et al., where the effect was determined to be saturated after a 15 min hold (Haasen and Kelly, 1957). The samples that were partially unloaded also demonstrated the yield point, lower in magnitude than those that were fully unloaded (with and without a hold). This is also consistent with the findings of Haasen et al., as they stated that the full effect is not seen unless the sample is unloaded by more than 50 pct (Haasen and Kelly, 1957). The results presented support that both effects are at play, but strain aging exhibited a larger effect, based on the observation that $\text{Δ}\sigma$ was highest at large strains. At large strains, more strain induced martensite is available for strain aging. It may be assumed that due to carbon and nitrogen supersaturation in martensite as well as high dislocation densities, strain induced martensite will experience more strain aging, corresponding to a higher $\text{Δ}\sigma$. This behavior was demonstrated in a TRIP700 steel, in which the behavior was also attributed to short-time strain aging (Mendiguren et al., 2015). For short-time strain aging, the Snoek rearrangement of interstitial atoms is activated due to the stress-induced rearrangement of carbon within the lattice. This indicates that the magnitude of the increase in yield stress is proportional to the interstitial content of the steel (Mendiguren et al., 2015).

A model of the amount of work converted to heat during deformation was used to calculate the expected temperature of the samples. This model does not account for any heating due to the exothermic austenite to martensite transition. The predicted temperature of the sample is given by Andrade-Campos et al. (2010).

$T=T_{RT}+\frac{0.9{{{\displaystyle \int }}^{\text{}}}_0^{\mathit{ϵ}}\sigma d\mathit{ϵ}}{\rho C}(2)$

where T_RT is the ambient temperature (21.4°C), ρ is the density of the steel and has the value of 7,860 kg m⁻³ (Callister, 2007), C is the specific heat of the steel and has the value of 495 J°C⁻¹ kg⁻¹ (Callister, 2007), and ${{{\displaystyle \int }}^{\text{}}}_0^{\mathit{ϵ}}\sigma d\mathit{ϵ}$ is the area under the stress strain curve to a given strain, ϵ. Using this model, the samples tested here are expected to accumulate less than 5°C during each interrupted strain increment. During the monotonic testing of the samples, this model predicts nearly 100°C of heating over the entire test. However, the monotonic tests to failure took just under 14 min to complete, which resulted in little heat accumulation within the sample.

Both a change in properties due to a hold and due to an unload are relevant to forming operations, as they may be designed to be multi-step, or to vary the load at specific locations within the part to allow for material flow. Though, an increase in yielding may cause higher local stresses needed for a part to be plastically deformed after initial straining. The stresses observed in interrupted testing were up to a 3 pct increase in stress required for deformation, which may cause the strain distribution of the part to vary from what it was intended due to local flow stress changes.

5 Conclusion

Interrupting and changing strain path in an austenitic stainless-steel introduces a yield point that has been attributed to strain aging and adiabatic heating in literature and resembles the Haasen-Kelly effect. Based on a model from literature, the samples were expected to accumulate less than 2°C during interrupted straining, which does not support the yield point being due to sample heating during deformation. The samples did show a time dependence on the magnitude of the yield point exhibited, as well as a dependence on the amount of unloading that occurred during testing. Based on the results shown, the yield point may be due to a combination of the Haasen-Kelly effect and strain aging of the sample. The increase in yield stress observed can cause up to a 3 pct increase in stress required for deformation, which may have implications during multi-step forming operations. This behavior provides a potential area of improvement for yield criteria, because sequential loading and unloading changes the subsequent deformation behavior in a way that has not been accounted for in existing yield criteria.

Data Availability Statement

The raw data supporting the conclusions of this article will be made available by the authors, without undue reservation.

Author Contributions

MT conceptualization, formal analysis, investigation, writing - original draft, visualization. CF investigation, writing - review and editing. AC writing - review and editing, supervision. KC writing - review and editing, supervision.

Funding

This program is supported by NSF Award 1752530, Career: Controlling Austenite Stability and Response During Deformation of Advanced High Strength Steels, through the Division of Civil, Mechanical and Manufacturing Innovation and the Advanced Steel Processing and Products Steel Center at the Colorado School of Mines.

Conflict of Interest

The authors declare that the research was conducted in the absence of any commercial or financial relationships that could be construed as a potential conflict of interest.

Acknowledgments

The authors would like to acknowledge Trevor Ballard and Kayla Molnar for their input and aid in mechanical testing as well as the Advanced Steel Processing and Products Research Center at the Colorado School of Mines for their support.

References

Alturk, R., Hector, L. G., Enloe, C. M., Abu-Farha, F., and Brown, T. W. (2018). Strain rate effect on tensile flow behavior and anisotropy of a medium-manganese trip steel. JOM. 70, 894–905. doi:10.1007/s11837-018-2830-3

CrossRef Full Text | Google Scholar

Andrade-Campos, A., Teixeira-Dias, F., Krupp, U., Barlat, F., Rauch, E., and Grácio, J. (2010). Effect of strain rate, adiabatic heating and phase transformation phenomena on the mechanical behaviour of stainless steel. Strain. 46, 283–297. doi:10.1111/j.1475-1305.2008.00572.x

CrossRef Full Text | Google Scholar

Billur, E., and Altan, T. (2012). Challenges in forming advanced high strength steels. Proc. New Develop. Sheet Met. Form., 285–304.

Google Scholar

Callister, W. D. (2007). Materials science and engineering an introduction. New York, NY: John Wiley.

Google Scholar

Coryell, J., Savic, V., Hector, L., and Mishra, S. (2013). Temperature effects on the deformation and fracture of a quenched-and-partitioned steel. Tech. rep. [Equb ahead of print].doi:10.4271/2013-01-0610

CrossRef Full Text | Google Scholar

Dieter, G. (1976). Mechanical metallurgy. New York, NY: McGracw-Hill.

Google Scholar

Finfrock, C. B., Clarke, A. J., Thomas, G. A., and Clarke, K. D. (2020). Austenite stability and strain hardening in c-mn-si quenching and partitioning steels. Metall. Mater. Trans. 51, 2025–2034. doi:10.1007/s11661-020-05666-8

CrossRef Full Text | Google Scholar

Haasen, P., and Kelly, A. (1957). A yield phenomenon in face-centered cubic single crystals. Acta Metall. 5, 192–199. doi:10.1016/0001-6160(57)90165-7

CrossRef Full Text | Google Scholar

Hecker, S., Stout, M., Staudhammer, K., and Smith, J. (1982). Effects of strain state and strain rate on deformation-induced transformation in 304 stainless steel: part i. magnetic measurements and mechanical behavior. Metall. Trans. A. 13, 619–626. doi:10.1007/BF02644427

CrossRef Full Text | Google Scholar

Hill, R. (1948). A theory of the yielding and plastic flow of anisotropic metals. Proc. Roy. Soc. Lond. Math. Phys. Sci. 193, 281–297. doi:10.1098/rspa.1948.0045

CrossRef Full Text | Google Scholar

Holmedal, B. (2019). Bauschinger effect modelled by yield surface distortions. Int. J. Plast. 123, 86–100. doi:10.1016/j.ijplas.2019.07.009

CrossRef Full Text | Google Scholar

Lewis, D. T. (1999). Influence of compositional variation on deformation induced martensite formation in type 304 stainless steels. PhD thesis. Golden, CO: Colorado School of Mines, Arthur Lakes Library.

Google Scholar

Lichtenfeld, J. A., Van Tyne, C. J., and Mataya, M. C. (2006). Effect of strain rate on stress-strain behavior of alloy 309 and 304l austenitic stainless steel. Metall. Mater. Trans. 37, 147–161. doi:10.1007/s11661-006-0160-5

CrossRef Full Text | Google Scholar

Mendiguren, J., Cortés, F., Gómez, X., and Galdos, L. (2015). Elastic behaviour characterisation of trip 700 steel by means of loading–unloading tests. Mat. Sci. Eng. A. 634, 147–152. doi:10.1016/j.msea.2015.03.050

CrossRef Full Text | Google Scholar

Mises, R. v. (1913). Mechanics of solid bodies in the plastically-deformable state. Göttin Nachr. Math. Phys. 1, 582–592.

Google Scholar

Naghdi, P. M., Essenburg, F., and Koff, W. (1957). An experimental study of initial and subsequent yield surfaces in plasticity. Technical Report. (Accessed August 27, 2020).

Google Scholar

Rathbun, R., Matlock, D., and Speer, J. (2000). Strain aging behavior of austenitic stainless steels containing strain induced martensite. Scripta Materialia. 42, 887–891. doi:10.1016/S1359-6462(00)00308-0

CrossRef Full Text | Google Scholar

Streicher, A. M., Speer, J. G., and Matlock, D. K. (2002). Forming response of retained austenite in a c-si-mn high strength trip sheet steel. Steel Res. 73, 287–293. doi:10.1002/srin.200200210

CrossRef Full Text | Google Scholar

Tresca, H. (1864). Memoire sur l’écoulement des solides à de forte pressions. Acad. Sci. Paris. 2, 59.

Google Scholar

Tsuchida, N., Morimoto, Y., Tonan, T., Shibata, Y., Fukaura, K., and Ueji, R. (2011). Stress-induced martensitic transformation behaviors at various temperatures and their trip effects in sus304 metastable austenitic stainless steel. ISIJ Internat. 51, 124–129. doi:10.2355/isijinternational.51.124

CrossRef Full Text | Google Scholar

Zou, D., Li, S., He, J., Gu, B., and Li, Y. (2018). The deformation induced martensitic transformation and mechanical behavior of quenching and partitioning steels under complex loading process. Mat. Sci. Eng.: A. 715, 243–256. doi:10.1016/j.msea.2018.01.011

CrossRef Full Text | Google Scholar

Zou, D., Li, S., and He, J. (2017). Temperature and strain rate dependent deformation induced martensitic transformation and flow behavior of quenching and partitioning steels. Mat. Sci. Eng. A. 680, 54–63. doi:10.1016/j.msea.2016.10.083Get

CrossRef Full Text | Google Scholar