J. Mater. Sci. Technol. ›› 2020, Vol. 50: 204-214.DOI: 10.1016/j.jmst.2020.01.060
• Research Article • Previous Articles Next Articles
Zhihong Wu, Hongchao Kou*(), Nana Chen, Mengqi Zhang, Ke Hua, Jiangkun Fan, Bin Tang, Jinshan Li
Received:
2019-12-11
Revised:
2020-01-11
Accepted:
2020-01-27
Published:
2020-08-01
Online:
2020-08-10
Contact:
Hongchao Kou
Zhihong Wu, Hongchao Kou, Nana Chen, Mengqi Zhang, Ke Hua, Jiangkun Fan, Bin Tang, Jinshan Li. Duality of the fatigue behavior and failure mechanism in notched specimens of Ti-7Mo-3Nb-3Cr-3Al alloy[J]. J. Mater. Sci. Technol., 2020, 50: 204-214.
Ti | Mo | Nb | Cr | Al | Fe | O | N | C |
---|---|---|---|---|---|---|---|---|
Bal. | 7.14 | 3.00 | 3.10 | 3.04 | 0.05 | 0.12 | 0.009 | 0.018 |
Table 1 Chemical compositions of Ti-7333 alloy used in this study (wt%).
Ti | Mo | Nb | Cr | Al | Fe | O | N | C |
---|---|---|---|---|---|---|---|---|
Bal. | 7.14 | 3.00 | 3.10 | 3.04 | 0.05 | 0.12 | 0.009 | 0.018 |
Fig. 1. Picture (a) and schematic representation (b) (in mm, not to scale) of a cylindrical dog-bone-shaped notched specimen with Kt = 3. The blue dashed box shows the enlarged view of gage section of specimen with a circumferential V-notch.
Fig. 2. SEM/SE and TEM micrographs of Ti7333-A (a-c), Ti7333-B (d-f), and Ti7333-C (g-i). SEM/SE images (a and b, d and e, g and h) show the αp particles and transformed-β matrix (β+αs). TEM bright-field images (c, f and i) show the αs precipitates. The cross sections parallel to the loading direction were used for SEM microstructure observations.
ID | TMP routes | Vf of αp (%) | D of αp (μm) |
---|---|---|---|
Ti7333-A | 790 ℃ forging+820 ℃/1 h/FC → 765 ℃/1 h/AC + 520 ℃/6 h/AC | 20 | 5 |
Ti7333-B | 835 ℃ forging+820 ℃/1 h/FC → 765 ℃/1 h/AC + 520 ℃/6 h/AC | 23 | 4 |
Ti7333-C | 820 ℃/50 min/AC + 540 ℃/6 h/AC | 7 | 2 |
Table 2 Thermo-mechanical processing routes and corresponding microstructure descriptions of Ti-7333 alloy.
ID | TMP routes | Vf of αp (%) | D of αp (μm) |
---|---|---|---|
Ti7333-A | 790 ℃ forging+820 ℃/1 h/FC → 765 ℃/1 h/AC + 520 ℃/6 h/AC | 20 | 5 |
Ti7333-B | 835 ℃ forging+820 ℃/1 h/FC → 765 ℃/1 h/AC + 520 ℃/6 h/AC | 23 | 4 |
Ti7333-C | 820 ℃/50 min/AC + 540 ℃/6 h/AC | 7 | 2 |
Fig. 3. Tensile mechanical properties and fatigue strength of Ti-7333 alloy (YS: yield strength; UTS: ultimate tensile strength; EL: elongation; RA: reduction of area; FS: fatigue strength at 107 cycles and Kt = 3).
Fig. 4. (a) EBSD-derived phase map of the initial microstructure of Ti7333-B, (b) the corresponding inverse pole figure (IPF) map and (c) pole figures of selected α particles and β grain, showing that a majority of intragranular α particles obey the Burgers orientation relationship (BOR) with β phase. The cross-section parallel to the loading direction was used for EBSD testing.
Fig. 5. Two-stage S-N fatigue behavior in Ti7333-A (a), the dual S-N fatigue behavior in Ti7333-B (b) and Ti7333-C (c). Arrows denote that the tests were terminated when the specimen survived by 107 cycles.
Fig. 6. Typical fractographies of four notched specimens showing surface crack-initiation with- and without-facets. The overall fracture surface morphologies of Ti7333-A alloy specimen (σmax =400 MPa, Nf = 57900 cycles a, Ti7333-B alloy specimen σmax =330 MPa, Nf = 4.66 × 106 cycles) (d), Ti7333-C alloy specimen (σmax =340 MPa, Nf = 8.04 × 106 cycles) (g) and Ti7333-C alloy specimen (σmax =400 MPa, Nf = 3.408 × 106 cycles) (i); while magnified views of crack-initiation sites are shown in (b, e, h and k), and magnified views of crack-growth regions are shown in (c and f).
Fig. 7. FIB cross-section and EBSD characterization of a long-lifetime failure specimen microstructural arrangement (σmax =330 MPa, Nf = 4.66 × 106 cycles): (a) faceted αp particles and the neighboring grains shown on the FIB-CS; (b) EBSD-derived IPF//LD map of the crack-initiation neighborhood showing contiguous αp facets; Corresponding phase map are shown in (c); (d) the corresponding Kernel average misorientation (KAM) map showing the heterogeneous distribution of KAM values between αp phase and β phase. {110} slip traces and 3D-view of crystal are superimposed on maps. Schmid factor values for each slip system in β grain are listed here.
ID | Euler angles | The angles of base normal respective to LD | Spatial angle of facet | ||
---|---|---|---|---|---|
φ1 | Ф | φ2 | |||
F1 | 21.1° | 125.2° | 26.6° | 43° | 44° |
F2 | 17.7° | 125.1° | 15.8° | 38° | |
F3 | 19.4° | 122.0° | 31.7° | 44° |
Table 3 A comparative analysis of the angles of base normal respective to loading direction (LD) and spatial angle of facet plane.
ID | Euler angles | The angles of base normal respective to LD | Spatial angle of facet | ||
---|---|---|---|---|---|
φ1 | Ф | φ2 | |||
F1 | 21.1° | 125.2° | 26.6° | 43° | 44° |
F2 | 17.7° | 125.1° | 15.8° | 38° | |
F3 | 19.4° | 122.0° | 31.7° | 44° |
ID | Basal {0002}<11-20> | Prismatic {10-10}<11-20> | Pyramidal {10-11}<11-20> | First-order pyramidal {10-11}<11-23> | Second-order pyramidal {11-22}<11-23> |
---|---|---|---|---|---|
N1 | 0.34 | 0.40 | 0.43 | 0.37 | 0.38 |
F1 | 0.49 | 0.20 | 0.37 | 0.41 | 0.27 |
F2 | 0.48 | 0.20 | 0.39 | 0.42 | 0.30 |
F3 | 0.48 | 0.15 | 0.33 | 0.42 | 0.29 |
N2 | 0.47 | 0.31 | 0.46 | 0.32 | 0.17 |
Table 4 Schmid factors for αp particles (the highest Schmid factor values are shown in bold text).
ID | Basal {0002}<11-20> | Prismatic {10-10}<11-20> | Pyramidal {10-11}<11-20> | First-order pyramidal {10-11}<11-23> | Second-order pyramidal {11-22}<11-23> |
---|---|---|---|---|---|
N1 | 0.34 | 0.40 | 0.43 | 0.37 | 0.38 |
F1 | 0.49 | 0.20 | 0.37 | 0.41 | 0.27 |
F2 | 0.48 | 0.20 | 0.39 | 0.42 | 0.30 |
F3 | 0.48 | 0.15 | 0.33 | 0.42 | 0.29 |
N2 | 0.47 | 0.31 | 0.46 | 0.32 | 0.17 |
Fig. 9. (a) EBSD-derived IPF//LD map of the fatigued microstructure from Ti7333-A showing the crystallographic orientation of α and β phases. (b) The corresponding phase map showing the distribution of α phase and β phase. (c) The corresponding KAM map with step size of 50 nm showing the heterogeneous distribution of KAM values between αp phase and βt matrix. The insets of local misorientation angle distribution shows that the β phase has a larger percentage of high misorientation angle distribution.
Fig. 10. TEM micrographs showing the dislocation structures of the fatigued microstructure in the crack-initiation region: (a) bright field image showing significant dislocation tangles in the β+αs matrix; (b) HAADF image showing the subgrain boundary in the faceted αp particle. The SAED patterns taken from (b) are shown in (c, d and e).
Fig. 11. Schematics for phenomenological models for fatigue crack-initiation: (a) the dislocation pileup is formed at αp phase boundaries at the beginning of fatigue loading; (b) the basal dislocation pile up is formed within αp particle until a dislocation through phase boundary, leaving a residual boundary dislocation. The residual boundary dislocations continue to accumulate to a critical value, leading to facet formation along basal plane of αp particles under the tension stress, followed by short crack propagates along (110) slip plane with the highest Schmid factor value.
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