Change in dislocation configuration of deformed Fe-Ni-Nb-Ti-C-B alloy during stress relaxation

Transmission electron microscopy (TEM) was applied to investigate theevolution of dislocation configuration and strain induced precipitation behavior during relaxationprocess after deformation in Fe-Ni-Nb-Ti-C-B alloy. Experimental results indicate that thedislocation density is very high and distribute randornly before relaxation. As the relaxation timeincreasing, dislocation cells will form gradually by polygonization. The strain inducedprecipitation retards the progress. In the final relaxation stage, most dislocations get rid ofpinning of precipitates and the cells have developed into subgrains with large size.

VARIATION OF SUBSTRUCTURES OF PEARLITIC HEAT RESISTANT STEEL AFTER HIGH TEMPERATURE AGING

The observations of dislocations, substructures and other microstructural details were conducted mainly by means of transmission electron microscope (TEM) and scanning electron microscope (SEM) for 12CrlMoV pearlitic heat-resistant steel. It is shown that during the high temperature long-term aging, the disordered and jumbled phase-transformed dislocations caused by normalized cooling are recovered and rearranged into cell substructures, and then the dislocation density is reduced gradually. Finally a low density linear dislocation configuration and a stabler dislocation network are formed and ferritic grains grow considerably.

Dislocation behavior in Cu single crystal joints under the ultrasonically excited high-strain-rate deformation

The coupling effects of ultrasonic excitation and high-strain-rate deformation are the core factors for weld formation during ultrasonic welding.However,interfacial deformation behavior still shrouds in uncer-tainty because of the contradictory features between mutual dislocation retardation caused by severely frictional deformation and ultrasonic-accelerated dislocation motion.[101]and[111]-oriented Cu single crystals which tended to form geometrically necessary boundaries(GNBs)were selected as the welding substrates to trace the uniquely acoustoplastic effects in the interfacial region under the ultrasonically excited high-strain-rate deformation.It was indicated that for a low energy input,micro-welds localized at the specific interface region,and equiaxed dislocation cells substituting for GNBs dominated in the ini-tial single crystal rotation region.As the welding energy increased,continuous shear deformation drove the dynamic recrystallization region covered by equiaxed grains to spread progressively.Limited discrete dislocations inside the recrystallized grains and nascent dislocation cells at the grain boundaries were ob-served in[101]and[111]joints simultaneously,suggesting that the ultrasonic excitation promoted motion of intragranular dislocation and pile-up along the sub-grain boundaries.The interfacial morphology be-fore and after expansion of recrystallization region all exhibited the weakening of orientation constraint on dislocation motion,which was also confirmed by the similar micro-hardness in joint interface.The first-principle calculation and applied strain-rate analysis further revealed that ultrasonic excitation en-hanced dislocation slipping,and enabled dislocation motion to accommodate severe plastic deformation at a high-strain-rate.

IMPROVEMENT ON FATIGUE LIFE OF ALLOY LY12CZ AFTER LASER RADIATION AND ITS DAMAGE EVOLUTION

The change of microstructure of fatigue specimens before and after laser radiation was studied by transmission electron microscopy.The results show that the diameter of dislocation cell λ tends to a constant at fatigue failure.Based on the principles of continuous damage mechanics,expressions of the fatigue damage criterion and processes of fatigue damage evolu- tion for L Y12CZ have been derived.

DEFORMATION AND STRENGTHENING OF COLD-DRAWN STEEL WIRES

It was shown by the study of TEM that the fine lamellar pearlite becomes a ductile phase dur- ing cold drawing.There exist many ledges to emit dislocations at Fe_3C/Fe interface.It is one of the reasons that high density of dislocations emerges at the Fe_3C/Fe interface. Furthermore,there are some evidences to support that dislocation cuts through Fe_3C.There- fore,it is necessary to consider the contribution of cementite being sheared strengthening.

Heat treatment effects on the metastable microstructure,mechanical property and corrosion behavior of Al-added CoCrFeMnNi alloys fabricated by laser powder bed fusion

With the development of aerospace and transportation,high-strength structural materials manufactured by additive manufacturing techniques get more attention,which allows the production of counterparts with complex structures.This work investigates Al-added CoCrFeMnNi high-entropy alloys(Al-HEAs)pre-pared by laser powder bed fusion(PBF-LB),adding 4.4 wt.%Al reducing approximately 7%density.The contribution of post-heat-treatment to microstructure,mechanical properties,and corrosion behaviors are explored.Hot cracking along with grain boundaries in the as-built PBF-LB Al-HEAs is determined,which comes from the residual liquid film as a larger solidification temperature range by adding Al.The PBF-LB Al-HEAs mainly consist of a face-centered cubic(FCC)matrix with Al/Ni/Mn decorated dislocation cells therein and a minor body-centered cubic(BCC)phase.Upon 850℃ annealing treatment,massive BCC phases(ordered NiAl and disordered Cr-rich precipitates)generate at the dislocation cell/grain bound-aries and the dislocation cells are still retained.However,the volume fraction of BCC phases and the dislocation cells vanish after 1150℃ solution treatment.As a result,Al-HEA850 shows an over 1000 MPa yield strength with nearly no ductility(<3%);the Al-HEA1150 exhibits considerable strength-ductility properties.Meanwhile,the Al-HEA850 demonstrates the worst pitting corrosion resistance due to the preferential dissolution of the NiAl precipitates in chloride-containing solutions.After comparatively de-liberating the evolution of strength-ductility and localized corrosion,we built a framework about the effects of the heat treatment on the mechanical property and degradation behavior in additively manu-factured Al-added high-strength HEAs.

Microstructural Evolutions of AA7055 Aluminum Alloy Under Dynamic and Quasi-static Compressions

The microstructural evolution of AA7055 aluminum alloy under dynamic impact loading with the strain rate of 1.3 × 10^4 s^-1 controlled by a split Hopkinson pressure bar was investigated, and compared with that under quasi-static mechanical loading in compression with strain rate of 1.0 × 10^-3 s^-1. The quasi-static-compressed sample exhibited equiaxed dislocation cells, which were different from the elongated and incomplete dislocation cells for the alloy undergoing dynamic compression. The high strain-rate compression also induced the formation of localized shear bands in which the recrystallizations characterized as fine equiaxed grains were observed. The microstructural evolutions under both quasi-static and dynamic compressions are rationalized in terms of the dislocation cell model combined with the dislocation kinetics, in addition to the adiabatic temperature rise in shear bands at high strain rate.

Revisiting the Hierarchical Microstructures of an Al-Zn-Mg Alloy Fabricated by Pre-deformation and Aging

Pre-deformation before aging has been demonstrated to have a positive effect on the mechanical strength of the 7N01 alloy in our previous study,which is rather different from the general negative effects of pre-deformation on high-strength 7XXX aluminum alloys.In order to explain the strengthening mechanism relating to the positive effect,in the present study,the microstructure of the aged 7N01 alloy with different degrees of pre-deformation was investigated in detail using advanced electron microscopy techniques.Our results show that,without pre-deformation,the aged alloy is strengthened mainly by the η′type of hardening precipitates.In contrast,with pre-deformation,the aged alloy is strengthened by the hierarchical microstructure consisting of the GP-η′type of precipitates formed inside sub-grains,the ηp type of precipitates formed at small-angle boundaries,and the dislocation introduced by pre-deformation(residual work-hardening effect).By visualizing the distribution of theηp precipitates through three-dimensional electron tomography,the 3 D microstructures of dislocation cells are clearly revealed.Proper combinations of ηp precipitates,GP-η′precipitates and residual dislocations in the alloy are responsible for the positive effect of pre-deformation on its mechanical properties.

Effects of hydrogen charging and deformation on tensile properties of a multi-component alloy for nuclear applications

In this study,the influence of hydrogen charging and deformation on the tensile behavior of a 60Fe-12Cr-10Mn-15Cu-3Mo multi-component alloy was investigated using electron microscopy and positron annihilation lifetime spectroscopy.The results show that hydrogen-induced vacancy clusters found in the electrochemically charged hydrogen specimens are responsible for crack initiation.Upon ingress to the microstructure,hydrogen promotes the formation of cell-structured dislocations that are beneficial for the improvement of tensile strength.In addition,hydrogen embrittlement can be mitigated by dislocations that can hinder hydrogen mobility in the deformed specimens.