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Acta Metall Sin  2015, Vol. 51 Issue (11): 1297-1305    DOI: 10.11900/0412.1961.2014.00541
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TENSILE DEFORMATION BEHAVIOR OF HYDROGEN CHARGED ULTRAHIGH STRENGTH STEEL STUDIED BY IN SITU NEUTRON DIFFRACTION
Pingguang XU1(),Jiang YIN2,Shuyan ZHANG3
1 Japan Atomic Energy Agency, Tokai, Ibaraki, 319-1195 Japan
2 Jiangsu Asian Star Anchor Chain Co. Ltd., Jingjiang 214533
3 Rutherford Appleton Laboratory, Didcot OX11 0QX United Kingdom
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Abstract  

The tensile deformation behavior and the axial lattice strain response of 1250 MPa ultra-high strength steels with and without hydrogen charging were comparably investigated using time-of-flight neutron diffraction together with the fracture morphology and microstructure observation. Before tensile loading, the axial (110) lattice plane spacing of hydrogen charged specimen was found larger than that of non-charged specimen while the axial (200) lattice plane spacing of the former was smaller than that of the latter, suggesting that the hydrogen atoms occupied the tetrahedral site promoted the increment of axial (110) lattice plane spacing while the balanced internal stress resulted in the proper decrement of axial (200) lattice plane spacing. The necking and ductile fracture after approaching the 1250 MPa tensile strength occurred in the non-charged specimen, while the brittle fracture occurred in the 8.0×10-6 hydrogen charged specimen at 500 MPa holding during step-by-step loading. The neutron diffraction analysis showed that in the non-charged specimen, the linear elastic deformation was kept up to 500 MPa loading, the nonlinear elastic deformation was observed preferably on the axial (200) reflection at 700 MPa, and then on the axial (110) reflection at 800 MPa; the axial {200} (i.e. <200>//TD, TD—tensile direction) grain orientation-dependent microyielding was observed preferably at 800 MPa while the (211) reflection was still under linear elastic deformation. Comparably, in the hydrogen charged specimen, the nonlinear elastic deformation was observed preferably on the axial (110) reflection at 300 MPa, and then on the axial (200) reflection at 400 MPa; the axial {110} grain orientation-dependent microyielding was observed preferably at 400 MPa while the axial (211) reflection was still under linear elastic deformation. The longitudinally sectioned microstructure observation under fracture surface confirmed the typical <110>-oriented tensile fiber texture in the non-charged specimen while the intergranular cracks along grain boundaries, quasi-cleavage/cleavage cracks and local crystal rotation in various grains of the hydrogen charged specimen. A concept about crystallographic orientation dependent microyielding was employed here to explain the above results, i.e. the hydrogen charging promoted the axial {110} grain orientation-dependent microyielding rather than axial {200} grain orientation-dependent microyielding, and the diffusible hydrogen embrittled the matrix microstructure, accompanying with local plastic deformation.

Key words:  brittle fracture      hydrogen charging      local plastic deformation      high strength low alloy steel      neutron diffraction      lattice strain     
Fund: Supported by National Key Scientific Instrument and Equipment Development Projects (No.2011YQ030112)

Cite this article: 

Pingguang XU,Jiang YIN,Shuyan ZHANG. TENSILE DEFORMATION BEHAVIOR OF HYDROGEN CHARGED ULTRAHIGH STRENGTH STEEL STUDIED BY IN SITU NEUTRON DIFFRACTION. Acta Metall Sin, 2015, 51(11): 1297-1305.

URL: 

https://www.ams.org.cn/EN/10.11900/0412.1961.2014.00541     OR     https://www.ams.org.cn/EN/Y2015/V51/I11/1297

Fig.1  Thermal desorption analysis curve of diffusional hydrogen in the hydrogen charged and zinc-plated high strength steel specimen after 120 h air exposure at 5~7 ℃
Fig.2  Step-by-step tensile deformation and fracture responses
Fig.3  Peak shift of (110) and (200) diffraction peaks of non-charged specimen during step-by-step tensile deformation[25]
Fig.4  Changes in macroscopic strain and &lt;hkl&gt;//TD orientation-dependent lattice strain of non-charged specimen during step-by-step tensile deformation (TD—tensile direction) [25]
Fig.5  Peak shift of (110) and (200) diffraction peaks of hydrogen-charged specimen during step-by-step tensile deformation
Fig.6  Changes in macroscopic strain and &lt;hkl&gt;//TD orientation-dependent lattice strain of hydrogen-charged specimen during tensile deformation
Specimen Lattice parameter (110) interplanar (200) interplanar (211) interplanar
spacing spacing spacing
Non-charged, No.1 2.86968±0.00003 2.02929±0.00003 1.43502±0.00006 1.17151±0.00003
Hydrogen charged, No.2 2.86967±0.00002 2.02932±0.00002 1.43488±0.00004 1.17151±0.00002
Change in No.2 and No.1 -0.00001 0.00003 -0.00014 0.00000
Hydrogen charged, No.3 2.86971±0.00003 2.02936±0.00002 1.43490±0.00005 1.17154±0.00002
Change in No.3 and No.1 0.00003 0.00007 -0.00012 0.00003
Table 1  Full refinement lattice parameter and single peak fitted interplanar spacing before loading
Fig.7  Fracture morphologies of non-charged specimen (a, b) and hydrogen-charged specimen (c~e)
Fig.8  Microstructures near longitudinally sectioned fracture of in situ tensile specimens, where the inverse pole figure mappings were obtained according to the tensile direction
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