versión impresa ISSN 1516-1439
versión On-line ISSN 1980-5373
Mat. Res. v.9 n.1 São Carlos ene./mar. 2006
Roberto Braga FigueiredoI, *; André Luiz de Moraes CostaII; Margareth Spangler AndradeII; Maria Teresa Paulino AguilarIII; Paulo Roberto CetlinI
IMetallurgical and Materials Engineering Department, Universidade Federal de Minas Gerais, Rua Espírito Santo, 35, Centro, 30160-030 Belo Horizonte - MG, Brazil
IIMetallurgical Technology Division, Fundação Centro Tecnológico de Minas Gerais, Av. José Candido da Silveira, 2000, 31170-000 Belo Horizonte - MG, Brazil
IIIMaterials and Civil Construction Department, Universidade Federal de Minas Gerais, Rua Espírito Santo, 35, Centro, 30160-030 Belo Horizonte - MG, Brazil
Equal Channel Angular Pressing (ECAP) is the most prominent SPD (Severe Plastic Deformation) method for the production of ultrafine and nanostructured metals, and has been extensively employed and analyzed. This technique was applied to a Pb-4%Sb alloy at room temperature, in order to study its effect on a low melting point and multiphase metallic material. The material was subjected to effective strains higher than 9, after 8 passes of processing, where dynamic and static recrystallization are expected during and after each pass. This eliminates any grain refinement and allows the analysis only of the microstructural effects associated with second phase redistribution and eventual precipitate dissolution. ECAP followed route C, which eliminates structural alignment after each even ECAP pass, facilitating the study of the microstructural evolution. It is shown that three ECAP passes are necessary to completely break the lamellar structure of the as cast strucure and that antimony dissolves into the lead rich matrix. Dynamic recrystallization and structural changes reduce the material strength and change the flow curve format.
Keywords: equal channel angular extrusion, Pb-Sb alloy, dynamic recrystallization
Severe plastic deformation (SPD) has been arousing great scientific interest, especially due to its capacity of producing materials which display unusual properties1. One of the advantages of some of the SPD methods is the possibility of achieving fabrication rates and costs comparable to those for the production methods of conventional materials, making use of equipments similar to those used in conventional deformation processing2.
Equal-Channel Angular Pressing (ECAP) is the most prominent SPD technique, due to its capability of producing bulk workpieces free of porosity and inclusions3. There has been also attempts to adapt this technique to continuous processing, enabling the production of materials in a large scale, efficient and cost effective manner4.
During ECAP the workpiece is extruded through two intersecting channels with the same cross sections. The angle between the channels is defined as F5 as shown in Figure 1. One important advantage of ECAP process is that it can be repeated several times without changing the workpiece dimensions and the applied strain can be increased to any level. ECAP allies severe strains and a simple shear deformation mode that contribute to strong, sometimes unusual effects on properties and structure5.
Iwahashi et al.6 derived a relationship to calculate the imposed strain, e, in one cycle of ECAP as a function of the angles F and Y (angle of the external curvature of the deformation zone see Figure 1).
Most common dies used in the process have angle F between 90° and 120° and angle y between 0° and 180° - F. In these dies the strain for one ECAP cycle is approximately 1. In order to attain adequate microstructural refinement through SPD, strains higher than 4 are usually required and thus multiple ECAP cycles are performed. One important parameter in the microstructural evolution through multiple processing cycles is the workpiece rotation between repetitive extrusions. The angle of rotation defines the processing route and the most common are: route A, where the workpiece is not rotated between cycles, route B, involving a rotation of 90° of the sample between successive passes, and route C, where this angle of rotation is 180°. Route B is the most efficient one for microstructural refinement3. It is important to emphasize, in the present situation, that route C is associated only with a shear reversal at each suceeding pass; this means that for each even-numbered pass, the spatial distortion of the microstructure is eliminated, allowing a comparison with the original, pre-ECAP microstructure.
In SPD processes, metals are intensely strained under high pressure. For the case of materials not undergoing dynamic recrystallization (DRX) during the deformation or static recrystalization (SRX) after the straining, the dislocations introduced into the crystalline lattice are rearranged into cells that evolve to new grains7. Such grain refining has been exhaustively studied, and grain sizes as fine as 300 nm8 and 210 nm9 were produced in copper, smaller than 400 nm in aluminum alloys1,10 and as fine as 200 nm in low carbon steel11,12. Ultrafine grain structures were also reported in titanium13. SPD also leads to dramatic increases in mechanical strength1,8,9 for non-recrystallizing materials, where high strain rate superplastic forming capability was obtained in several non-superplastic alloys14-16. Changes in other metal properties such as ultimate solubility10, diffusion coefficient17 and Young´s modulus18 were also reported for metals processed by ECAP. For example, in the specific case of an Al-Fe alloy, it has been reported that SPD causes the partial dissolution of the iron rich precipitates in this alloy, with iron re-dissolving into the Al matrix10.
The present paper presents an analysis of the use of ECAP Route C to a low melting point, multiphase, as cast Pb-4%Sb alloy. In the as-cast state, this alloy displays an eutectic, regular structure of a Sb rich phase, which is thoroughly broken by ECAP. Route C in ECAP is associated only with a reversion of shear for every even numbered pass, yielding an undistorted microstructure in relation to the initial, pre-ECAP situation. This allows a comparison of the initial, as cast microstructure, with the microstructures after each even numbered ECAP passes. The Pb recrystallization temperature is below 0 °C19, and it is expected that the present Pb-Sb alloy will undergo dynamic and static recrystallization at room temperature, leading to no grain refinement effects caused by ECAP. One can thus evaluate the effects of the redistribution of the second phase and of the recrystallization of the matrix on the mechanical properties of the as-cast alloy, disconsidering the consequences of grain size changes. Finally, since reports in the literature mention the partial dissolution of precipitates in metals submitted to SPD, probably caused by an enhanced solubility of the matrix10, one can investigate the fact for the present Sb rich precipitates.
2. Experimental Procedure
The ECAP die was constructed using ABNT/SAE 1045 quenched and tempered steel. The angle between channels (F) is 90° and the angle of external curvature (y) is 0°. According to Equation 1 the effective strain per pass is 1.15. The die cross section is square with 16 mm edge. Figure 2 shows a picture of the die.
A Pb-4%Sb alloy was prepared by melting the pure elements and pouring into an aluminum mold. Square section bars were machined into workpieces with dimensions of 16 x 16 x 120 mm.
ECAP was carried out at room temperature with MoS2 as lubricant and with punch velocity of 20 mm/min in an INSTRON machine model 5582. The samples were rotated about the extrusion axis by 180° between each pass (route C) up to a total of 8 passes. This processing route imparts the smallest end-effects on the samples from multiple ECAP pressings. This effect occurs due to the regions of the billet that do not cross the shear plane during processing and so are not strained as the rest of the billet. The ends of the billets are usually eliminated after pressings to avoid the propagation of end-effects, leading to a decrease of the billet during multiple pressings. However the regions that do not cross the shear plane are the same during multiple passes with route C and so the end-effects are restrict to a limited length, and the cutting of the billet edges after pressing is not required.
Samples of as-cast and processed materials were prepared for microstructural analysis by cutting, grinding and polishing with diamond and colloidal silica. Samples of the longitudinal and cross sections were observed. The microstructure was revealed after etching the samples with a solution of acetic acid plus H2O2. The specimens were observed by Scanning Electron Microscopy at 25 kV using either a JEOL JSM 6360 LV or a JEOL JC XA 733 microscopes. Vickers microhardness tests were performed with a Leitz Wetzlar machine with a load of 5 gf.
Cylindrical workpieces for compression tests were machined from the as cast and the ECAP - processed material. They had 10 mm diameter and 15 mm height. Compression tests were performed at an INSTRON machine with constant cross head displacement of 1 mm/min.
3. Results and Discussion
Figure 3a shows the microstructure of the as-cast alloy, displaying a typical dendritic microstructure. The bright phase is the lead rich matrix and the dark phase corresponds to lamelar antimony rich precipitates, formed in the eutectic reaction.
The longitudinal microstructures of the alloy extruded with 1 and 2 passes are presented in Figures 3b and 3c, respectively. It is observed that after the first pass the structure attains a preferential orientation at an angle of 27° with the extrusion direction. As already discussed, the reversed shear associated to successive ECAP passes following route C eliminates the alignment after each even-numbered pass. This is clearly seen in Figure 3c, which can thus be compared with Figure 3a.
The as-cast structure was well refined after the first pressing, as shown in Figures 4 (cross section of the billet) and 5 (longitudinal section of the billet). The Pb recrystallization temperature is below 0 °C19, so it is expected that the material recrystallizes during the process and after it. As the grain boundaries do not show the same alignment of the dendrites (see Figure 5) and the same grain structure is observed in the longitudinal and cross section, it is believed that recrystallization occurred after the shear straining.
Figure 6 shows the microstructure of the material after 8 ECAP passes. It was observed that the regions with a higher number of small, broken precipitates commonly display a finer grain size.
Figure 7 shows the evolution of the precipitate distribution in the Pb-Sb alloy after 1, 2 and 8 ECAP passes. The first pass broke some precipitates, as seen in Figure 7b, but there still remains some larger ones. After the second pass almost all precipitates were broken into small particles (see Figure 7c). Figure 7d shows that further straining seems to reduce the size and the quantity of the particles. It is here important to note that the complete break up of the original as-cast structure seems to occur only after a few ECAP passes.
Figure 8a shows the backscattered electron image of the alloy in the as-cast condition, whereas figure 8b presents the same image of the material after 2 passes of ECAP. Figure 8c shows an enlarged view of a typical region in Figure 8b. The darker regions in Figure 8b, which are seen in more detail around the precipitates in Figure 8c, are antimony rich regions, which are not observed in the as-cast structure (Figure 8a). The lighter regions in Figures 8b and 8c correspond to grain boundaries and other topographic effects in the Pb matrix, caused by etching. This indicates that ECAP caused some dissolution of the antimony rich phase, similarly to the reports in the literature for precipitates in an Al-Fe alloy10.
Figure 7 also indicates that the grain size did not change with an increasing number of ECAP passes. This is confirmed through Figure 9, which displays the evolution of the grain size with the number of passes by ECAP. This result was already expected for this alloy, and one concludes that recrystallization occurred after all extrusion passes, similarly to the situation analyzed by Im et al.20, that applied ECAP to a Bi2Te3-Sb2Te3 cast. They noted that recrystallization occurred after ECAP and that the recrystallized grains exihibited the same size after all passes.
The material flow curves, determined by compression tests of the material in the as cast condition and after 1 pass of ECAP, are presented in Figure 10. They suggest that dynamic recrystallization occurs during room temperature deformation of the material both in the as cast and after ECAP conditions. There is an initial strain hardening behavior up to a peak stress followed by flow softening and deformation under constant stress. However, the results after ECAP display a considerably lower stress level and a much smaller peak strain, in relation to the as-cast structure (0.22 for the former and 0.56 for the latter). This indicates that the microstrucutural changes caused by ECAP, involving the redistribution and break up of the second phase structure, introduces profound changes in the strength and in the recrystallization behavior of the material. The precipitate distribution after ECAP triggers dynamic recrystallization (possibly around these precipitates) more promptly than in the case of the as-cast material. At least a part of the softening of the material caused by ECAP is associated with the earlier occurence of DRX in this material, as compared with the as-cast material.
The microhardness of the alloy decreased after the first pass and remained almost unchanged with further passes, as shown in Figure 11a. On the other hand, the expected decrease of the punch force associated with lower microhardness was slower than the fall in the microhardness (see Figure 11b), although the degree of decrease is approximately the same in both cases (about 50% of the initial value). The punch force reached the minimum value only after the third ECAP pass. The microhardness is connected basically to the local changes in mechanical properties of the material, and the abrupt fall in this property after a single ECAP pass is probably caused by the recrystallization in the material during and after the pass. On the other hand, the punch force reflects not only the local strength changes, but also the overall strengthening effect associated with the second phase distribution in the material, as well as the dynamic recrystallization kinetics of the material. Figure 7 shows that a certain number of ECAP passes is necessary to completely redistribute the second phase structure. This redistribution also accelerated the dynamic recrystallization of the alloy (see Figure 10), probably due to the nucleation of recrystallized regions around the broken second phase particles. Considering the punch force evolution in Figure 11b, one concludes that only after 3 ECAP passes, following route C, does the microstructure of the as-cast alloy stabilize into a situation typical of ECAP processing.
An as-cast Pb-4%Sb alloy, processed by Equal Channel Angular Extrusion (ECAP) in up to 8 passes and reaching an accumulated effective strain of 9, displays a recrystallized matrix of the material after each ECAP pass.
The average grain size of the material is stable, at around 10 mm, after all the individual passes. Some grain size heterogeneity was observed, and finer grains prevail in regions were small, grouped precipitates dominate.
There are indications that the antimony rich precipitates in the as-cast structure undergo some degree of dissolution, caused by the ECAP processing.
The microstructural changes caused by ECAP in the as-cast structure of the material softens the material, due to the break-up of the original precipitate structure and to the acceleration of the dynamic recrystallization of the material, which begins for strains roughly 50% below that for the as-cast material.
The original microstructure of the as-cast material is broken by the ECAP, but evidence from the required punch force for each pass suggests that at least 3 ECAP passes through route C are necessary for the complete break-up of the original microstructure.
The authors are grateful for BRASIAÇO Ltda. for the construction of the ECAP die and for CNPq and PRONEX for the financial support.
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Received: December 2, 2004; Revised: December 8, 2005