“…The dissenting results of a relatively homogeneous cross section of the present material in comparison with the other studies using a laser beam 37,38 could be due to different thickness reductions, different α′‐martensite fractions after cold rolling and different beam parameters. However, the most important difference between investigations in previous studies 37,38 seems to be the chemical composition of the studied steel resulting in different reversion mechanism. The reversion behaviour was investigated on steel AISI 301LN, which is known to undergo a diffusional reversion (cf 16,53 …”
Section: Discussionmentioning
confidence: 49%
“…Thus, neither nonreverted α′‐martensite nor a significantly heterogeneous grain size distribution over the cross section was revealed. This is in contradiction to former reports on the microstructure after heat treatment by the one‐sided application of either an EB 39 or a laser beam 37,38 . The investigations on EB 39 reversion treatment were based on steel with comparable chemical composition and sheet thickness (3 mm) but a lower thickness reduction of 70% and an α′‐martensite fraction of 51 vol.% (cf., 7 same material as 39 ).…”
Section: Discussionmentioning
confidence: 59%
“…Comparing the different laser heat treatments, the slowest LS with 4.5 mm/s as expected led to the highest peak temperatures (Figure 3A) and vice versa (Figure 3C). As all other beam parameters were kept constant, the heat input is the higher the slower the laser beam speed is along the steel sheet 37 . The laser heat treatments at LS = 4.5 mm/s and LS = 6.0 mm/s exhibit average peak temperatures of 989°C and 779°C, respectively, both with a relatively small standard deviation of about 5°C (see Table S1 for listing of all recorded peak temperatures).…”
Section: Resultsmentioning
confidence: 99%
“…As all other beam parameters were kept constant, the heat input is the higher the slower the laser beam speed is along the steel sheet. 37 The laser heat treatments at LS = 4.5 mm/s and LS = 6.0 mm/s exhibit average peak temperatures of 989 C and 779 C, respectively, both with a relatively small standard deviation of about 5 C (see Table S1 for listing of all recorded peak temperatures). In contrast, in the case of LS = 7.0 mm/s, an average peak temperature of 608 C was recorded with a high standard deviation of about 44 C. This high scatter for the highest LS probably stems from a more sensitive influence of the exact position of the thermocouple in relation to the oscillation of the laser beam as F I G U R E 3 Signals of the thermocouples attached to the bottom of the steel sheets for the laser heat treatments at the linear speeds the wavelength of the laser's path on the material slightly increases from 2.8 mm for LS = 6.0 mm/s to 3.4 mm for LS = 7.0 mm/s.…”
Section: Laser Reversion Heat Treatmentmentioning
confidence: 99%
“…The laser and EB technologies, for example, offer a very local heat input, but on the other hand, the one‐sided application of the heat source impedes a uniform microstructure and grain size over the cross section. Consequently, previous studies 37–39 reported a difference between the top and bottom surface of the steel sheets. However, in case of Heinze et al 39 investigating steel with similar chemical composition as the present work, the grain size gradient over the cross section was reduced using appropriate scan strategies and EB parameters.…”
Different grain sizes were created in a metastable 17Cr-7Mn-7Ni steel by martensite-to-austenite reversion at different temperatures using a laser beam. Two fully reverted material states obtained at 990 C and 780 C exhibited average grain sizes of 7.7 and 2.7 μm, respectively. The third microstructure (610 C) consisted of grains at different stages of recrystallization and deformed austenite. A hot-pressed, coarse-grained counterpart was studied for reference. The yield and tensile strengths increased with refined grain size, maintaining reasonable elongation except for the heterogeneous microstructure. Total strain-controlled fatigue tests revealed increasing initial stress amplitudes but decreasing cyclic hardening and fatigue-induced α 0-martensite formation with decreasing grain size. Fatigue life was slightly improved for the 2.7-μm grain size. Contrary, the heterogeneous microstructure yielded an inferior lifetime, especially at high strain amplitudes. Examinations of the cyclically deformed microstructure showed that the characteristic deformation band structure was less pronounced in refined grains.
“…The dissenting results of a relatively homogeneous cross section of the present material in comparison with the other studies using a laser beam 37,38 could be due to different thickness reductions, different α′‐martensite fractions after cold rolling and different beam parameters. However, the most important difference between investigations in previous studies 37,38 seems to be the chemical composition of the studied steel resulting in different reversion mechanism. The reversion behaviour was investigated on steel AISI 301LN, which is known to undergo a diffusional reversion (cf 16,53 …”
Section: Discussionmentioning
confidence: 49%
“…Thus, neither nonreverted α′‐martensite nor a significantly heterogeneous grain size distribution over the cross section was revealed. This is in contradiction to former reports on the microstructure after heat treatment by the one‐sided application of either an EB 39 or a laser beam 37,38 . The investigations on EB 39 reversion treatment were based on steel with comparable chemical composition and sheet thickness (3 mm) but a lower thickness reduction of 70% and an α′‐martensite fraction of 51 vol.% (cf., 7 same material as 39 ).…”
Section: Discussionmentioning
confidence: 59%
“…Comparing the different laser heat treatments, the slowest LS with 4.5 mm/s as expected led to the highest peak temperatures (Figure 3A) and vice versa (Figure 3C). As all other beam parameters were kept constant, the heat input is the higher the slower the laser beam speed is along the steel sheet 37 . The laser heat treatments at LS = 4.5 mm/s and LS = 6.0 mm/s exhibit average peak temperatures of 989°C and 779°C, respectively, both with a relatively small standard deviation of about 5°C (see Table S1 for listing of all recorded peak temperatures).…”
Section: Resultsmentioning
confidence: 99%
“…As all other beam parameters were kept constant, the heat input is the higher the slower the laser beam speed is along the steel sheet. 37 The laser heat treatments at LS = 4.5 mm/s and LS = 6.0 mm/s exhibit average peak temperatures of 989 C and 779 C, respectively, both with a relatively small standard deviation of about 5 C (see Table S1 for listing of all recorded peak temperatures). In contrast, in the case of LS = 7.0 mm/s, an average peak temperature of 608 C was recorded with a high standard deviation of about 44 C. This high scatter for the highest LS probably stems from a more sensitive influence of the exact position of the thermocouple in relation to the oscillation of the laser beam as F I G U R E 3 Signals of the thermocouples attached to the bottom of the steel sheets for the laser heat treatments at the linear speeds the wavelength of the laser's path on the material slightly increases from 2.8 mm for LS = 6.0 mm/s to 3.4 mm for LS = 7.0 mm/s.…”
Section: Laser Reversion Heat Treatmentmentioning
confidence: 99%
“…The laser and EB technologies, for example, offer a very local heat input, but on the other hand, the one‐sided application of the heat source impedes a uniform microstructure and grain size over the cross section. Consequently, previous studies 37–39 reported a difference between the top and bottom surface of the steel sheets. However, in case of Heinze et al 39 investigating steel with similar chemical composition as the present work, the grain size gradient over the cross section was reduced using appropriate scan strategies and EB parameters.…”
Different grain sizes were created in a metastable 17Cr-7Mn-7Ni steel by martensite-to-austenite reversion at different temperatures using a laser beam. Two fully reverted material states obtained at 990 C and 780 C exhibited average grain sizes of 7.7 and 2.7 μm, respectively. The third microstructure (610 C) consisted of grains at different stages of recrystallization and deformed austenite. A hot-pressed, coarse-grained counterpart was studied for reference. The yield and tensile strengths increased with refined grain size, maintaining reasonable elongation except for the heterogeneous microstructure. Total strain-controlled fatigue tests revealed increasing initial stress amplitudes but decreasing cyclic hardening and fatigue-induced α 0-martensite formation with decreasing grain size. Fatigue life was slightly improved for the 2.7-μm grain size. Contrary, the heterogeneous microstructure yielded an inferior lifetime, especially at high strain amplitudes. Examinations of the cyclically deformed microstructure showed that the characteristic deformation band structure was less pronounced in refined grains.
Austenitic Cr–Ni stainless-type 301LN steel was subjected to a double-reversion annealing (DRA) treatment to develop bulk grain-refined microstructures. The tensile properties and formability of the DRA structures were determined by high-speed tensile and Erichsen cupping tests at a strain rate of 1.5 s−1 (50 mm s−1) and compared with those of coarse-grained steel. Detailed microstructural features of the DRA structures were characterized using the electron backscatter diffraction technique and X-ray diffraction analysis. The DRA structures achieved by annealing for 1 second at 800 °C and 900 °C exhibited a superior combination of yield (~ 950 and 770 MPa, respectively) and tensile (~ 1050 and 950 MPa, respectively) strengths and ductility (~ 35 and 40 pct, respectively, as well as reasonable Erichsen index values under high-speed biaxial strain. Due to adiabatic heating, the DRA structures had higher austenite stability during high-speed stretch forming, i.e., were less prone to strain-induced martensitic transformation. The finite-element method (FEM) was used to conduct coupled field thermomechanical analyses of the high-speed deformation processes for the coarse-grained and DRA structures. Comparison of the FEM analyses with the experimental results revealed a considerable influence (~ 20 pct) of martensitic transformation on the adiabatic temperature rise. The balance of the yield strength and Erichsen index value of the developed nanograined microstructure is comparable to that of coarse-grained commercial steel.
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