尖锐晶界角对柱状晶铜排伸长率的显著影响及机理-有色金属在线

简介概要

尖锐晶界角对柱状晶铜排伸长率的显著影响及机理

来源期刊：中国有色金属学报(英文版)2018年第7期

论文作者：石章智王海鹏刘雪峰

文章页码：1329 - 1333

关键词：铜；断裂；晶界角；伸长率；柱状晶

Key words：copper; fracture; grain boundary corner; elongation; columnar grain

摘要：研究柱状晶铜排在小变形量冷拉拔后伸长率显著下降的原因。通过温型连铸技术制备铜排，在多个应变量停止拉伸测试以探测裂纹源，采用电子背散射衍射(EBSD)技术分析位错滑移带。研究发现，铸态铜排中存在与连铸方向近平行的尖锐晶界角，拉拔后铜排的伸长率由铸态的68.8%骤降至拉拔态的18.8%。在尖锐晶界角附近发生更剧烈的塑性变形，局部应力集中甚至使Schmid因子低至0.17的位错滑移系启动。尖锐晶界角附近塑性变形的集中促使裂纹萌生和扩展，最终导致拉拔态铜排伸长率的显著降低。

Abstract: The reason why elongation of copper bars with columnar grains drops significantly after small cold-drawing was explored. The copper bars were prepared by warm-mould continuous casting. Tensile test was interrupted at various tensile strains in order to detect crack origin. Electron backscattered diffraction (EBSD) was used to analyze dislocation slip bands. It is found that the as-cast microstructure contains sharp grain boundary (GB) corners nearly parallel to the solidification direction (SD). Elongation of the copper bars drops significantly from 68.8% in as-cast state to 18.8% in as-drawn state. It is revealed that plastic deformation becomes severer in the vicinity of sharp GB corners. Locally accumulated internal stress even activates a slip system with very low Schmid factor of 0.17. The localized plastic deformation near sharp grain boundary corner promotes crack initiation and propagation, which eventually leads to the significant drop of elongation.

Trans. Nonferrous Met. Soc. China 28(2018) 1329-1333

Significant influence of sharp grain boundary corner on tensile elongation of copper bars with columnar grains and its mechanism

Zhang-zhi SHI¹, Hai-peng WANG¹, Xue-feng LIU^1,2

1. School of Materials Science and Engineering, University of Science and Technology Beijing, Beijing 100083, China;

2.Beijing Laboratory of Metallic Materials and Processing for Modern Transportation, University of Science and Technology Beijing, Beijing 100083, China

Received 9 March 2017; accepted 18 September 2017

Key words: copper; fracture; grain boundary corner; elongation; columnar grain

1 Introduction

An as-cast polycrystalline copper ingot usually has equiaxed grains or columnar grains or both, depending on its specific casting process [1-8]. Its tensile elongation is influenced by trace elements, strain rate, grain shape, grain size, and grain orientation [9-16]. An as-cast copper rod with continuous columnar grains exhibits an extraordinary ability of elongation along the direction of continuous casting. Such a copper rod with 17.3 mm in diameter can be reduced to 19.7 mm in diameter through a series of cold forming processes without annealing [17]. Stress state of a cold forming process is usually different from that of a tensile test. Metals often exhibit larger elongation in cold forming process than that in tensile test. As shown in Fig. 1, the tensile elongation of copper varies widely. Cold drawing results in a decrease of tensile elongation due to the well-known work-hardening effect, which is lowered by about 20% through a small area reduction of 20% (Fig. 1).

Intragranular dislocation slip behavior, interaction between dislocations and grain boundaries (GBs), and interaction between dislocations and defects are main causes of the drop of tensile elongation [18-21]. Previous studies on influence of GB corners on ductility mainly focus on GB triple junctions. In modelling, a GB corner ending at a triple junction is supposed to have an angle of 120° [21-26]. However, in practice, a polycrystalline copper usually contains GB corners with various angles. Sharp GB corners should have a significant influence on the ductility of copper.

2 Experimental

Copper bars with 99.9% Cu were prepared by a self-developed warm-mould continuous casting technology. They have a uniform size of 20 mm×8 mm×1000 mm. The transverse, normal and solidification directions of the as-cast copper bars are designated as TD, ND and SD, respectively. A sketch of warm-mould continuous casting is shown in Fig. 2(a). The temperature of the graphite mould is controlled between 900 and 1000 °C, which is lower than the melting temperature of pure copper (i.e., T_m=1083 °C).

Fig. 1 Decrease of tensile elongation of polycrystalline copper with accumulated area reduction after cold drawing without annealing [3-5]

Fig. 2 Sketch of copper bar produced by self-developed warm-mould continuous casting (a), sketch of cold drawing of copper bars (b) and specimens of as-cast and as-drawn copper bars for tensile tests (c) (unit: mm)

Out of the exit of the graphite mould, water is used for strong cooling. As shown in Fig. 2(b), the as-cast copper bars were cold drawn along the SD through a single pass with an area reduction of 20.3%. Their size changes to be 17 mm × 7.5 mm × 1254.9 mm. The transverse, normal and drawing directions of the as-drawn copper bars are designated as TD, ND and DD, respectively. The semi-angle of the drawing die is 9°, with mineral oil as lubricant.

Specimens for tensile tests are shown in Fig. 2(c). In order to observe slip bands, their surfaces were ground, mechanically polished, and then electro-polished. The electro-polishing was conducted at room temperature, 10 V for 15 s, with a solution of 100 mL H₃PO₄, 100 mL C₂H₅OH, 200 mL H₂O, 2 g NH₂CONH₂ and 20 mL CH₃CH(OH)CH₃. Tensile tests were performed using a WDW-10E electronic universal testing machine. The tensile loading direction (LD) was parallel to the SD or the DD, with a strain rate of 1×10^-3s^-1. Specimens were etched for 5 s by a solution of 5% FeCl₃ and 95% ethanol for microstructure observation using a Zeiss Axio Scope A1 optical microscope. Grain orientations were measured by a Zeiss Auriga field emission scanning electron microscopy (FESEM) equipped with a detector of electron backscattered diffraction (EBSD). The measured EBSD data were post-processed using Matlab MTEX toolbox [27].

3 Results and discussion

A representative microstructure of the as-cast copper with columnar grains is shown in Fig. 3(a). The lengths of the grains are about parallel to the SD, which vary widely from 1 to more than 17 mm. There exist sharp GB corners about parallel to the SD with GB angles ranging from 10° to 90°, locating at triple junctions or at GBs, as pointed out by arrows in Fig. 3(a). After the cold drawing along the SD, the GB corners become sharper. Meanwhile, they should produce stress concentration as can be expected from the theory of elasticity [28,29]. Engineering stress-strain curves of the as-cast and the as-drawn copper specimens are given in Fig. 3(b), showing a prominent work-hardening effect. The as-cast copper has a high elongation of 68.8%. However, after a single pass cold drawing with an area reduction of 20.3%, its elongation drops significantly to 18.8%. The drop is as large as 50%, which is considerably larger than that previously reported, as can be seen from Fig. 1.

Fig. 3 As-cast microstructure with sharp GB corners pointed out by arrows (a) and engineering stress-strain curves (R_p0.2, R_m and A refer to yield stress, maximum tensile stress and elongation, respectively) (b)

At a tensile strain of 16.0% before final fracture, cracking is detected around sharp GB corners, a representative one is shown in Fig. 4(a). In the figure, boundaries with misorientations larger than 10° are outlined in black. Kukuchi patterns in black regions cannot be indexed due to the absence of the material in cracks or severe lattice distortion caused by plastic deformation [30]. The EBSD image in Fig. 4(a) is colored according to inverse pole figure (IPF) along the DD. It can be seen that the DD is about parallel to 〈001〉 of Grain 1, while it is about parallel to〈111〉of Grain 2. With measured Euler angles provided in the upper right part of Fig. 4(a), the average misorientation between Grains 1 and 2 is calculated to be 42.4°. The GB angle of the sharp GB corner of Grain 2 is about 38°. Crack at its tip is much larger than that at its base, indicating that stress concentration is much more serious at the tip.

Fig. 4 SEM image and its correspoding EBSD image of sharp GB corner at tensile strain of 16.0% (In EBSD image, boundaries with misorietations larger than 10° are outlined in black. Pole figures and the maximum Schmid factors of slip systems are calculated using measured Euler angles) (a), SEM image of triple junction formed by three grains with three GB corners of obtuse angles larger than 100° at tensile strain of 16.0% (b), fracture morphology viewed from ND at tensile strain of 18.8% (c), fracture morphology viewed from DD (d) and sketch of fracture mechanism of as-drawn copper with columnar grains (e)

Combining the SEM image with its corresponding EBSD image in Fig. 4(a), the slip systems corresponding to the slip bands on the surface of the tensile test specimen can be determined. The measured Euler angles of Region A in Grain 1 are 162°, 154° and 162°. Accordingly, its {111} pole figure and the maximum Schmid factors (SFs) of each {111} slip system can be calculated, as given in Fig. 4(a). According to the geometry of pole figure, a line normal to the line connecting the center of a pole figure and the pole of a plane is the trace of the plane on the observed surface [31]. So, it can be determined that , and slip bands appear in Region A, the SFs of which are larger than 0.40. However, only and slip bands appear in Grain 1 in regions far away from the crack. Dense slip bands appear in a narrow region starting at the crack, indicating severer plastic deformation due to stress concentration.

Inhomogeneous plastic deformation is common in a large grain, resulting in misorientation between regions within the grain [32]. For example, in Grain 1, the misorientation between Region B and Region A is 7.3°. So, slip band trace in Region B deviates from that in Region A. Such a deviation is obvious for slip band, as can be seen from the pole figures in Fig. 4(a). In Region B near the crack, additional slip bands with SF of 0.41 are observed due to stress concentration. Similarly, in Grain 1 close to the crack through Region C, , and slip bands with high SFs are also observed (Fig. 4(a)). While in Grain 2 nearby, , and slip bands are observed, SFs of which are 0.44, 0.31 and 0.17, respectively. Comparatively, in Grain 2 far away from the crack, only slip band with the highest SF is observed. Therefore, the abnormal appearance of slip band with a rather low SF is due to stress concentration around the crack.

At the same tensile strain of 16.0%, a triple junction formed by Grains 3-5 with three blunt GB corners is shown in Fig. 4(b). The angles of GB corners of Grains 3-5 in the figure are measured to be 112.6°, 110.2° and 137.2°, respectively. In the vicinity of the triple junction, no cracks are detected. Such kind of blunt GB corner is common in copper with equi-axed grains or continuous columnar grains. Compared Fig. 4(b) with Fig. 4(a), it is clear that sharp GB corners promote the formation of cracks.

The cracks that preferentially formed around sharp GB corners propagate rapidly under the applied tensile loading, resulting in fracture at a strain of 18.8%. The fracture morphology viewed from the ND is shown in Fig. 4(c). A large section of the fracture orients about 68° from the LD, while the rest is about normal to it. The fracture morphology viewed from the DD is shown in Fig. 4(d), in which many dimples are observed, indicating a ductile fracture. The mechanism of the dramatic elongation drop is sketched in Fig. 4(e). Sharp GB corners about parallel to the SD exist in an as-cast copper bar with columnar grains. After cold drawing along the SD, they are sharpened and concentrate stress. Since the LD of the tensile test is also along the SD, the stress concentration becomes more serious, resulting in severe plastic deformation around the sharp GB corners. Therefore, cracks preferentially form around them and propagate rapidly, which eventually causes fracture.

4 Conclusions

1) Copper bars with columnar grains, prepared by a self-developed warm-mould continuous casting technology, have a high elongation of 68.8%. However, after a single pass cold drawing with an area reduction of 20.3%, their tensile elongation drops significantly to 18.8%.

2) Sharp grain boundary corners are found in the as-cast copper bars, which are about parallel to the solidification direction. After the cold drawing along this direction, they are sharpened and concentrate stress. Since the tensile loading is also applied along this direction, the stress concentration becomes more serious. Different from the regions far away within a grain, those close to the sharp grain boundary corners deform more seriously, in which more types of slip bands are observed, with smaller spacing or even with a rather low Schmid factor. Therefore, cracks preferentially form around the sharp grain boundary corners and propagate rapidly until fracture happens eventually. The sharp grain boundary corners greatly enhance inhomogeneous plastic deformation, which contributes greatly to the significant elongation drop.

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