1 Introduction
2 Materials and Methods
2.1 Materials
AHSS Generation | Strength Level (MPa) | Steel Denomination | Thickness (mm) | Supplier |
---|---|---|---|---|
1st GEN | 780 | DP780 | 1.5 | Voestalpine |
TRIP780 | 1.6 | ArcelorMittal | ||
980 | DP980 | 1.35 | Voestalpine | |
3rd GEN | 1180 | 3rd Gen DP1180 | 1.2 | Voestalpine |
3rd Gen TBF1180 | 1.4 | ArcelorMittal | ||
3rd Gen Q&P1180 | 1.5 | ArcelorMittal |
Steel Grade | C | Si | Mn | Cr | B | Al | Ti |
---|---|---|---|---|---|---|---|
DP780 | ~ 0.15 | < 0.9 | < 2.0 | < 0.7 | < 0.003 | ~ 0.05 | < 0.0060 |
TRIP780 | ~ 0.20 | ~ 1.60 | ~ 1.70 | ~ 0.02 | < 0.001 | ~ 0.05 | ~ 0.0070 |
DP980 | ~ 0.15 | < 0.5 | ~ 2.3 | < 0.7 | < 0.003 | ~ 0.05 | < 0.0060 |
3rd Gen DP1180 | ~ 0.20 | < 2.0 | ~ 2.5 | < 0.7 | < 0.003 | ~ 0.05 | < 0.0060 |
3rd Gen TBF1180 | ~ 0.23 | < 2.0 | < 2.9 | < 0.7 | < 0.005 | ~ 0.04 | ~ 0.0070 |
3rd Gen Q&P1180 | ~ 0.18 | < 2.0 | < 2.9 | < 0.7 | < 0.005 | ~ 0.03 | ~ 0.0060 |
Steel | Microstructure | RA Volume Fraction, Vγ (Pct) |
---|---|---|
DP780 | F/B matrix, M/RA islands | 9.8 |
TRIP780 | F/B matrix, M/RA islands | 15.6 |
DP980 | F/B matrix, TM, M islands, RA | 5.5 |
3rd Gen DP1180 | UB/LB matrix, M/RA islands and laths | 14.8 |
3rd Gen TBF1180 | carbide-free B matrix, M/RA islands and laths of RA | 15.5 |
3rd Gen Q&P1180 | TM matrix, B, M/RA islands and laths of RA | 12.6 |
2.2 Experimental Procedure
2.2.1 Uniaxial tensile tests
2.2.2 Fracture toughness
2.2.3 Hole expansion tests
3 Results
3.1 Uniaxial Tensile Properties
Steel | YS (MPa) | UTS (MPa) | YS/UTS (–) | UE (Pct) | TE (Pct) | n2-4 (–) | TUE (–) | TFS (–) | TTS (–) | UTSxTE (MPa*Pct) |
---|---|---|---|---|---|---|---|---|---|---|
DP780 | 513 | 823 | 0.62 | 14.2 | 19.9 | 0.20 | 0.13 | 0.48 | 0.45 | 16378 |
TRIP780 | 542 | 851 | 0.64 | 20.7 | 25.8 | 0.20 | 0.19 | 0.49 | 0.25 | 21956 |
DP980 | 816 | 1055 | 0.77 | 6.54 | 9.7 | 0.13 | 0.06 | 0.57 | 0.57 | 10234 |
3rd Gen DP1180 | 895 | 1212 | 0.74 | 10.5 | 14.3 | 0.15 | 0.10 | 0.49 | 0.51 | 17332 |
3rd Gen TBF1180 | 987 | 1216 | 0.81 | 9.2 | 12.6 | 0.11 | 0.09 | 0.55 | 0.57 | 15322 |
3rd Gen Q&P1180 | 1034 | 1191 | 0.87 | 9.2 | 13.1 | 0.09 | 0.09 | 0.63 | 0.64 | 15602 |
3.2 Fracture Toughness
3.2.1 Essential work of fracture
Steel | EWF | Thickness Strain DENT | HET | |||
---|---|---|---|---|---|---|
w
e
i
(kJ/m2) | we (kJ/m2) | ε
3f DENT
i
(–) | ε
3f DENT
p
(–) | HER (Pct) | TTSHET (–) | |
DP780 | 123 ± 14 | 151 ± 31 | 0.08 ± 0.01 | 0.17 ± 0.00 | 34 ± 3 | 0.11 ± 0.03 |
TRIP780 | 104 ± 14 | 106 ± 24 | 0.07 ± 0.00 | 0.14 ± 0.01 | 23 ± 3 | 0.08 ± 0.00 |
DP980 | 119 ± 25 | 149 ± 21 | 0.08 ± 0.01 | 0.11 ± 0.01 | 38 ± 1 | 0.11 ± 0.02 |
3rd Gen DP1180 | 105 ± 9 | 115 ± 20 | 0.05 ± 0.00 | 0.10 ± 0.01 | 32 ± 1 | 0.10 ± 0.02 |
3rd Gen TBF1180 | 90 ± 15 | 104 ± 30 | 0.06 ± 0.01 | 0.10 ± 0.03 | 28 ± 2 | 0.11 ± 0.02 |
3rd Gen Q&P1180 | 184 ± 14 | 196 ± 31 | 0.09 ± 0.02 | 0.14 ± 0.02 | 41 ± 4 | 0.12 ± 0.01 |
3.2.2 Fracture thickness strain from DENT specimens
3.3 Hole Expansion Tests
4 Discussion
4.1 Effect of the Microstructure on Mechanical Properties and Fracture Resistance
4.2 Correlation Between Stretch Flangeability and Fracture Resistance Parameters
4.3 Thickness Strain Measurements
4.4 Relation Between Tensile Properties and Fracture Toughness
4.5 AHSS Classification According to Their Crack Propagation Resistance
5 Conclusions
-
Conventional uniaxial tensile properties are not sufficient to describe the local formability and fracture behavior of AHSS. On the other hand, other fracture-related parameters such as the true fracture strain (TFS), the true thickness strain (TTS), or the specific essential work of fracture (we) provide a better prediction of fracture performance. The very good correlation between we and HER values for several AHSS and HSLA steels consolidates the observations made in previous work and confirms the close relationship between fracture toughness and stretch flangeability in AHSS.
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A new classification mapping considering global ductility (UE) and fracture resistance (we) is proposed for a more exhaustive description of the overall formability and fracture behavior of AHSS. The proposed diagram can be useful for improved AHSS performance ranking and optimum material selection depending on the requirements of the intended application.
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The true thickness strain (TTS) from uniaxial tensile tests significantly overestimates the thickness reduction in punched hole edge and fatigue pre-cracked DENT specimens. However, the relative differences in TTS are well reflected in toughness and edge cracking resistance parameters. Therefore, it might be used as a qualitative indicator of fracture toughness and edge fracture resistance.
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The values of thickness strain measured in fatigue pre-cracked DENT specimens (ε3f DENT) are similar to edge thinning values measured in HET specimens (TTSHET). This evidences the similarity between edge fracture and crack propagation mechanisms and allows establishing an objective fracture criterion for edge-cracking prediction. These results highlight the importance of addressing edge cracking phenomena considering the underlying fracture mechanisms, since fracture is governed by crack propagation resistance.
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The essential work of fracture is proposed here as a relevant parameter to assess the fracture resistance of AHSS and to understand the role of microstructural constituents on fracture behavior. The investigation on the correlation between fracture toughness and uniaxial tensile properties has shown that fracture toughness cannot be estimated from traditional ductility or toughness indicators (UE, TE, UTSxTE, etc.). Local strain measurements from tensile tests (TFS, TTS) offer a better estimation of fracture toughness. However, none of these parameters can accurately describe the fracture behavior in the presence of cracks. Therefore, fracture toughness, understood as the material’s crack initiation and propagation resistance, must be measured following a fracture mechanics approach to properly evaluate the microstructural effects on fracture behavior.
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The results obtained from fracture toughness tests revealed that microstructural features that improve global ductility, such as the TRIP effect, can have a detrimental effect on fracture toughness. Hence, microstructural design must take into account not only tensile properties but also crack initiation and propagation resistance parameters.