Microstructural evolution in adiabatic shear 243.pdfMicrostructural evolution in adiabatic shear...
Embed Size (px)
Transcript of Microstructural evolution in adiabatic shear 243.pdfMicrostructural evolution in adiabatic shear...
Acta Materialia 51 (2003) 13071325www.actamat-journals.com
Microstructural evolution in adiabatic shear localization instainless steel
M.A. Meyers a, Y.B. Xu b, Q. Xue a, M.T. Perez-Prado a, T.R. McNelley c,
a University of California, San Diego, La Jolla, CA 92093-0411, USAb Institute of Metals Research, Chinese Academy of Sciences, Shenyang 110016, China
c Naval Postgraduate School, Monterey, CA, USA
Received 15 February 2001; accepted 30 August 2002
Shear bands were generated under prescribed and controlled conditions in an AISI 304L stainless steel (Fe18%Cr8%Ni). Hat-shaped specimens were deformed in a Hopkinson bar at strain rates of ca 104 s1 and shear strains thatcould be varied between 1 and 100. Microstructural characterization was performed by electron backscattered diffraction(EBSD) with orientation imaging microscopy (OIM), and transmission electron microscopy (TEM). The shear-bandthickness was ca 18 m. This alloy with low-stacking fault energy deforms, at the imposed strain rates (outside ofthe shear band), by planar dislocations and stacking fault packets, twinning, and occasional martensitic phase transform-ations at twin-band intersections and regions of high plastic deformation. EBSD reveals gradual lattice rotations of thegrains approaching the core of the band. A  fiber texture (with the  direction perpendicular to both sheardirection and shear plane normal) develops both within the shear band and in the adjacent grains. The formation ofthis texture, under an imposed global simple shear, suggests that rotations take place concurrently with the shearingdeformation. This can be explained by compatibility requirements between neighboring deforming regions. EBSD couldnot reveal the deformation features at large strains because their scale was below the resolution of this technique. TEMreveals a number of features that are interpreted in terms of the mechanisms of deformation andrecovery/recrystallization postulated. They include the observation of grains with sizes in the nanocrystalline domain.The microstructural changes are described by an evolutionary model, leading from the initial grain size of 15 m tothe final submicronic (sub) grain size. Calculations are performed on the rotations of grain boundaries by grain-boundarydiffusion, which is three orders of magnitude higher than bulk diffusion at the deformation temperatures. They indicatethat the microstructural reorganization can take place within the deformation times of a few milliseconds. There isevidence that the unique microstructure is formed by rotational dynamic recrystallization. An amorphous region withinthe shear band is also observed and it is proposed that it is formed by a solid-state amorphization process; both theheating and cooling times within the band are extremely low and propitiate the retention of non-equilibrium structures.Published by Elsevier Science Ltd on behalf of Acta Materialia Inc.
Keywords: AISI 304L; Stainless steel; Shear bands; Adiabatic deformation; Twinning; Lattice rotation; Amorphization; Recrystallization
Corresponding author. Tel.: +1-831-656-2589; fax: +1-831-656-2238.
E-mail address: email@example.com (T.R. McNelley).
1359-6454/03/$30.00 Published by Elsevier Science Ltd on behalf of Acta Materialia Inc.doi:10.1016/S1359-6454(02)00526-8
The characterization of post-deformation micro-structures is a very important tool in the develop-
1308 M.A. Meyers et al. / Acta Materialia 51 (2003) 13071325
ment of our understanding of the thermo-mechan-ical evolution during shear localization. Thequestion of the correlation of the post-deformationstructure with the one evolving during deformationwill persist until real-time diagnostics will bedeveloped to characterize the microstructure withinthe shear bands as it is developing. Nevertheless,significant progress has been made by post-defor-mation observation and a number of structuralalterations have been either suggested or demon-strated. Whereas the older literature classified theshear bands into deformed and transformed(depending on their appearance as observed byoptical microscopy), it is now recognized that abroad range of structural alterations is possible:recovery, recrystallization (both dynamic andstatic), phase transformations, comminution (ofbrittle materials, amorphization, and crystallizationhave been discussed. The arsenal of the modernMaterials Scientist has recently gained the additionof a powerful new technique, electron backscatter-ing scanning microscopy [1,2]. This method, incombination with transmission electronmicroscopy (TEM), is helping the elucidation ofthe deformation/recovery mechanisms. It isimpossible to resolve the details of microstructureevolution within shear bands by optical or scanningelectron microscopy. Even TEM only reveals therecovered structure, which has undergone the plas-tic deformation and a complex thermo-mechan-ical history.
Mataya et al.  subjected a stainless steel tohigh-strain rate deformation and observed a dra-matic refinement in the grain size within the shearbands, that they attributed to dynamic recrystalliz-ation. Shortly thereafter, detailed observations byTEM were made by Stelly and Dormeval , Paket al. , Meyers and Pak , and Grebe et al. on shear bands produced in Ti6%Al4%V andcommercial purity Ti. The electron diffraction pat-terns inside and outside of the shear band were rad-ically different; outside the band, the characteristicpattern for a single crystalline orientation wasclear. Inside the band, a ring-like pattern, producedby many crystallographic orientations, was appar-ent. The shear band consisted of equiaxed grainswith diameters of 0.050.2 m. The dislocationdensity was relatively low. This remarkable feature
led to the suggestion by Meyers and Pak  thatthe structure was due to dynamic recrystallization.Dynamic recrystallization in Cu was first observedby Andrade et al. ; in Ti it was confirmedby Meyers et al. ; in tantalum, it was observedby Meyers et al. , Nesterenko et al. [12,13], andNemat Nasser et al. ; in AlLi alloys, Chenand Vecchio  and Xu et al. ;in brass, byLi et al. ; in steels, Beatty et al.  and Meun-ier et al.  observed equiaxed grains evensmaller (0.010.05 m).The shiny, transformedappearance reported by many investigators in shearbands in steels may be the result of a fine recrys-tallized structure with an associated dissolution ofcarbides, resulting in an increased resistance toetching. These features were in the past mistak-ingly identified as phase transformation products. The complex thermo-mechanical history ofmetals in the shear localization regions warrantsthe questions:
1. Do the observed recrystallized features occurduring or after plastic deformation?
2. What is the mechanism of recrystallization?
The goal of this contribution is to address thesequestions for an AISI 304L SS.
2. Experimental techniques
Shear bands were generated in the AISI 304LSS by two methods as follows.
2.1. The hat-shaped specimen method
The hat-shaped specimen method, using a splitHopkinson bar in the compression mode to gener-ate large shear strains in a small region (ca. 200m thick). This method, which was developed byMeyer and Manwaring ,has been successfullyused to generates shear localization regions in anumber of metals (Ti , steels , Al alloys, Ta [13,14]). It forces shear localization tooccur in a narrow region. Thus, even materials thatdo not localize spontaneously undergo localizationin this method. Fig. 1(a) shows a hat-shaped speci-men prior to and after being subjected to plastic
1309M.A. Meyers et al. / Acta Materialia 51 (2003) 13071325
Fig. 1. Schematic of experimental specimens and techniques. (a) Hat-shaped specimen; (b) thick-walled cylinder specimen.
deformation. Prescribed shear strains are obtainedby this method, and can be controlled by setting thethickness of the stopper ring. Stopper rings withdifferent thicknesses were used to control thedeformation. The displacement is shown in Fig.1(a). Fig. 2 shows the longitudinal section of hat-shaped specimen subjected to a displacement =1mm, yielding a shear strain of g100 if the bandwidth is taken as 10 m. Specimens were subjectedto displacements providing shear strains of 50, 75,and 100.
Fig. 2. Microstructure of shear band in stainless steel 304Lproduced in a hat-shaped specimen.
2.2. The explosive collapse of a thick-walledcylinder under controlled conditions
This technique was developed by Nesterenkoand Bondar  and applied to Ti ,stainlesssteel , and tantalum . Fig. 1(b) shows theinitial configuration of the hollow cylinder in theleft and a collapsed cylinder with the shear bandsindicated on the right. A regular pattern of spiralshear bands is produced. The inner diameter andthe thickness of the inner Cu tube establish the glo-bal strain. An explosive charge is placed on theoutside and produces, upon detonation, the sym-metric implosion of the cylinder. Shear bandsinitiated at the internal surfaces of the cylindersand propaged outwards along spiral trajectories.The height of the step in the inner surface providesthe displacement. The displacement, divided by thethickness of the bands, gives the shear strain. Rou-tinely, shear strains as high as 100 were obtained.Fig. 3 shows the pattern of shear bands observedon the inner surface of the deformed cylinder at anearly stage (ef=0.55); Fig. 3(b) shows the bandsat a larger strain (ef=0.92). It can be seen that thebands form with a characteristic spacing. As thebands grow, their spacing is increased. This occurs
1310 M.A. Meyers et al. / Acta Materialia 51 (2003) 13071325
Fig. 3. Shear band pattern at effective strains (a) e