Microstructure and texture development in AA3003 aluminium alloy

Journal Pre-proof Microstructure and texture development in AA3003 aluminium alloy Ranjeet Kumar, Aman Gupta, Tushar R. Dandekar, Rajesh K. Khatirkar

PII:

S2352-4928(19)30808-6

DOI:

https://doi.org/10.1016/j.mtcomm.2020.100965

Reference:

MTCOMM 100965

To appear in:

Materials Today Communications

Received Date:

4 September 2019

Revised Date:

27 January 2020

Accepted Date:

27 January 2020

Please cite this article as: Kumar R, Gupta A, Dandekar TR, Khatirkar RK, Microstructure and texture development in AA3003 aluminium alloy, Materials Today Communications (2020), doi: https://doi.org/10.1016/j.mtcomm.2020.100965

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Microstructure and texture development in AA3003 aluminium alloy Ranjeet

Kumar1,

Aman

Gupta2,

Tushar

Dandekar2,

R.

Rajesh

K.

Khatirkar2*

[email protected]

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Ranjeet Kumar1:E-mail: [email protected]

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Affiliation(s): 1Department of Materials Science and Engineering, Indian Institute of Technology Delhi, Hauz Khas, New Delhi -110016, India.

Aman Gupta2:E-mail: [email protected]

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2

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ORCID: orcid.org/0000-0001-5263-0539

Affiliation(s): 2Department of Metallurgical and Materials Engineering, Visvesvaraya National Institute

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ORCID: orcid.org/0000-0002-5833-7496

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of Technology (VNIT), South Ambazari Road, Nagpur- 440010, Maharashra, India.

Tushar Ramdas Dandekar2:E-mail: [email protected]

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Affiliation(s): 2Department of Metallurgical and Materials Engineering, Visvesvaraya National Institute of Technology (VNIT), South Ambazari Road, Nagpur- 440010, Maharashtra, India. ORCID: orcid.org/0000-0003-2391-0835 (4) Rajesh Kisni Khatirkar2 (*Corresponding author)

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E-mail:, [email protected]

Affiliation(s): 2Department of Metallurgical and Materials Engineering, Visvesvaraya National Institute of Technology (VNIT), South Ambazari Road, Nagpur- 440010, Maharashtra, India. Phone No: +919960973599, +91-712-2801508 Fax: +91-712-2223230 ORCID: orcid.org/0000-0001-6421-9368 1

Research highlights The initial as-cast material consisted of weak cube texture.

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After hot rolling, Brass, Cu, S, and Goss components developed.

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The hot rolled texture components strengthened after cold rolling.

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After annealing at 450ºC, weak cube was observed.

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Particle stimulated nucleation played an important role during recrystallization.

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Abstract

For good deep drawability in aluminium and its alloys, a proper balance of deformation and

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recrystallization texture components is essestial in the final material. This balance of deformation

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and recrystallization texture can only be achieved by properly controlling the thermo-mechanical processing of the alloy. In the present study, microstructure and texture development during casting, hot rolling, cold rolling, and annealing of an aluminum alloy (AA3003) is investigated.

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The cast microstructure showed large grains with average grain size 111 µm and presence of AlFe-Si particles along the grain boundaries. After hot rolling (500ºC (±10ºC)) and cold rolling, these second phase particles which consisted primarily of Fe:Si in a ratio 10:1 in the as-cast

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microstructure fragmented into smaller particles and had higher percentage of Fe, Mn, and Si. After hot rolling and cold rolling, microstructure showing banded structure along the rolling direction i.e. elongated grains. Annealing at 450ºC for 16 hours produced microstructure with uniform average grain size 22 µm and second phase particles with non-uniform size distribution. The initial as-cast AA3003 alloy had a very weak cube texture ({100}<100>, 3.4% volume fraction). After cold rolling, strong Brass ({110}<112>), Copper ({112}<111>) and S 2

({123}<634>) components formed. After cold rolling, cube decreased and did not improve significantly even after annealing at 450ºC. The developments in annealing texture is explained on the basis of particle stimulated nucleation.

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Keywords: Aluminium alloy, microstructure, texture, annealing, particle stimulated nucleation.

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1. Introduction

Aluminum (Al) and its alloys are most widely used for various applications in food

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industry, aerospace and automobiles industries because of their excellent properties like good

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strength-to-weight ratio, high corrosion resistance and easy manufacturing. Among various Al alloy, AA3003 alloy is most widely used for making kitchen utensils. Fe, Mn and Si are the

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major alloying elements in AA3003 alloy. Further, small amount of Ni, Mg, and Zn are also allowed, as this small deviation of composition doesn’t affect the manufacturing process and properties of this alloy significantly. The maximum solid solubility of Mg in Al is 1.8% at the eutectic temperature, and the addition of Mg reduces the melting temperature of aluminum

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[1,2]. The microstructure of AA3003 alloy consists of the Al matrix with Al15(Fe,Mn)3Si and Al6Mn second phase particles dispersed in it. Al6Mn containing 1.9%-4.1% Mn is the primary phase in this alloy [3]. During direct chill (DC) casting, the cooling rate from mould walls to the centre varies approximately from 20ºC/s to 0.5ºC/s in the ingot [4]. During normal solidification, primary dendrites of Al and alloying elements form until Al6Mn nucleation occurs. The nucleation of Al-Fe-Si-Mn particles is delayed due to slow cooling and during this period 3

dendrites of Al and Al6Mn grow in a competitive way. Fast cooling decreases the size of Al6Mn dendrites and the solid solution becomes saturated with Mn [5,6]. To achieve the desired thickness, cast ingot passes through the heated rollers, which reduces the thickness to approximately 25 mm. To avoid full recrystallization and fine precipitation, the temperature of hot rolling should not be very high. These fine precipitates hinder the grain boundaries migration

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during hot rolling and help in recrystallization when subjected to further annealing [7]. In subsequent cold rolling stage, large second phase particles of Al15(FeMn)3Si break and a large

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amount of stored energy is accumulated around these second phase particles. The stored energy helps to accelerate the recrystallization by particle stimulated nucleation (PSN) [8].

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The thickness reduction during hot rolling and cold rolling significantly affects the

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formability needed for shaping the alloy as it results in the changes in the texture of material. During forming, if the deformation texture obtained is not well balanced with the

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recrystallization texture, the formation of ears takes place in aluminium alloys during deep drawing. The control of texture is not simple in a hot rolling process due to recrystallization and

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deformation simultaneously. In aluminium alloys, the main concern is to obtained proper volume fraction of cube ({100}<100>) and deformation texture (Brass ({110}<112>), Copper ({112}<111>) and S ({123}<634>) components) to achieve good formability in the final product. In two phase particle containing alloys, PSN also affects the recrystallization process

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substantially further making the texture evolution complex along with variation in mechanical properties [7]. Presence of second phase particles also poses a challenge to improve its formability. The size, shape and distribution of second phase particles in the matrix plays usually a significant role in deciding the formability of two phase particle containing alloys. Deep drawability of sheet metals is usually linked with the intensity (or volume fraction) of texture

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components [9–13], r-bar and ∆r values. Earing is a common phenomenon in Al alloys during deep drawing, which is due to the higher ∆r values [12,14]. Rolling texture i.e. β-fibre (consisting of Brass, Cu and S) and recrystallized cube texture are the main causes of 45º and 0º/90º ears to rolling direction (RD), respectively. However, random texture and {111}˂uvw˃ orientations improve the deep drawability [15–18]. The texture components which forms in FCC

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Al alloys are Brass, Cu, S, Cube, r-Cube {001}˂110˃ and Goss {110}˂001˃. Brass, Cu and S forms during the cold rolling [19]. Recrystallization texture always originates from deformation

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texture [20]. Goss originates from Brass, while cube originates from deformed cube bands. Deformed Cube bands surrounded by S with a 40°<111> orientation relationship. Therefore

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grain boundaries of Cube bands have a high potential to nucleates cube texture [21]. Researchers

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have investigated the relationship between dislocation slipping and texture evolution to understand the aspects of geometrical rotation [22–24]. However, the studies on the evolution of

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microstructure and texture during thermo-mechanical processing of particle containing AA3003 alloy are rare. This has been the motivation for present investigation. The present study aims at

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understanding the evolution of microstructure and texture at various stages of thermo-mechanical processing for AA3003 aluminium alloy.

2. Experimental

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AA3003 alloy used in the present work went through four processes, namely casting, hot

rolling, cold rolling, and annealing. The initial material was cast in the form of small ingots of dimension 305 mm (length)×203 mm (width)×152 mm (thickness) and was used as the starting material in the present investigation. The chemical composition of the AA3003 alloy is given in Table 1. After casting, it was hot rolled at 500ºC (±10ºC) from 152 mm to 7 mm thickness under

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proper lubrication in multiple passes. Further reduction in thickness was carried out through cold rolling (at room temperature) from 7 mm to 2 mm. The cold-rolling was done in the direction perpendicular to the hot rolling direction. The cold rolled sheet was then annealed at 450ºC for 16 h. For further characterization, the material was cut into small samples of size 15 mm × 10 mm. All the samples were polished using SiC emery papers with successively fine particle size to reduce the surface roughness. Final polishing was done on a velvet cloth using suspension of

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alumina in distilled water (1μm particle size) followed by polishing with diamond suspension

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(0.1μm particle size). The samples were then etched with Kroll's reagent (92 ml distilled water, 6 ml nitric acid and 2 ml hydrofluoric acid) [25] to reveal the second phase particles. Bright field

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(BF) light optical microscopy (LOM) was done on a plane perpendicular to the transverse

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direction (TD). In order to observe the grain structure using polarized light optical microscopy (PLOM), samples were anodized with Barker’s reagent (a mixture of 20% fluoroboric acid and

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80% distilled water) [25]. For BF-LOM and PLOM, Zeiss Axiolab, Germany microscope equipped with Axiovision software was used. For scanning electron microscopy (SEM), JEOL

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6380A, Japan microscope was used in the secondary electron imaging mode. The images in SEM were captured at an accelerating voltage of 15kV, while the chemical composition of the second phase particles was determined with the help of Bruker XFlash 30 energy dispersive spectrometer (EDS) attached to SEM.

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For electron backscattered diffraction (EBSD), the samples were electropolished with a

mixture of methanol and perchloric acid (80:20 ratio) at -10°C and 11V DC for 15 sec after diamond polishing. An EDAX, USA EBSD system attached to FEI Quanta 300 field emission gun (FEG) SEM was used to obtain the EBSD data. The EBSD scans were taken at 1×1 binning with a step size of 0.2 μm for all samples. TSL-OIM analysis software (version 7.2) was used for

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post-processing of the EBSD data [26]. All the data points with confidence index (CI, which typically represents accuracy of indexing during EBSD data aquisition) less than 0.1 were removed during post processing. The bulk texture was measured for as-cast, hot rolled, cold rolled, and annealed AA3003 alloy samples at mid-thickness of the rolling plane (plane containg rolling direction RD and TD). A PANalytical XPert Pro MRD system in Schutlz reflection

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geometry equipped with CuKα radiation and point detector (Xenon filled) was used for the measurement of incomplete pole figures. Four incomplete pole figures - 111, 220, 200 and 311

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were measured upto a tilt angle of 75 for each sample. Defocusing correction was applied using a powdered AA3003 alloy sample. MATLAB based open source code MTEX was used for post-

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processing of the bulk texture data [27] by considering orthorhombic sample symmetry and

3. Results and discussion

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and size) of the second phase particle size.

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cubic crystal symmetry. ImageJ software was used to quantify the morphological details (shape

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Figure 1 shows the BF-LOM, PLOM and secondary electron SEM images of the as-cast sample. Figure 1(a) shows the presence of Al-Fe-Si particles in the microstructure. Also, the grain boundaries with these intermetallics particles in the Al matrix are visible as dark lines. Figure 1(b) shows the PLOM image indicating a very large grain size and dendritic structure in

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the microstructure. Fe and Si present in the aluminium alloy form hard and brittle intermetallic particles (also known as ‘chinese script morphology’ due to specific shape of precipitates) during casting (figures 1(c) and 1(d)). Precipitates with chinese script morphology formed at grain boundaries consists of many small branches of Al-Fe-Si-Mn intermetallic as confirmed by SEMEDS. The chinese script precipitate morphology forms during casting by ejecting out Fe and Si

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from the solution during solidification, since the solubility of Fe and Si in Al is very limited (the solubility of Si in Al is ∼1.65% at 577°C, and that of Fe in Al is ∼0.05% at 650°C) [28]. The thickness and size of these precipitates in chinese script morphology are affected by the solidification time (rate of cooling) [29]. Intermetallic particles, after casting mainly consists of Al, Fe, and Mn as shown in Table 2. This indicates the formation of unstable Al6(Fe,Mn)

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intermetallic. Initially, the size of these intermetallic was very large and consisted of lower Fe, Mn, and Si content which suggests the matrix had higher content of Fe, Mn, and Si in the form of

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solid solution leading to solid solution strengthening [30]. Figure 2 shows the BF-LOM, PLOM and secondary electron SEM images of the hot rolled sample. During hot rolling,

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recrystallization and deformation occur simultaneously, which allows large amount of

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deformation in single pass due to low work hardening rate at hot rolling temperatures. After hot rolling, the large dendritic grains deformed along RD (figures 2(a) and 2(b)) and large

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intermetallic particles (i.e. chinese script morphology) was broken into small intermetallic particles (figure 2(c)). After hot rolling, the intermetallic particles size were fairly uniform (as

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shown in figure 2(c)). The dendritic grains in the as-cast condition deformed during hot rolling and got elongated in an RD forming a banded structure. Mn, Fe, and Si diffusion took place as the hot rolling temperature was sufficient to initiate diffusion of elements present in the matrix. Increase in Fe, Mn, and Si content in intermetallic particles was observed (as given in table 2)

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during hot rolling, which also suggests the possible formation of α-Al12(Fe,Mn)3Si particles. In has been reported that unstable Al6(Fe,Mn) particles transform to stable α-Al12(Fe,Mn)3Si particles due to the diffusion of Mn, Si, and Fe during hot rolling. The diffusion of Mn provides nucleation sites for stable precipitation of α-Al12(Fe, Mn)3Si. The size of α-Al12(Fe, Mn)3Si particles were in the range of 0-6µm [31]. Figure 3 shows the BF-LOM, PLOM and secondary

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electron SEM images of the cold rolled sample. After cold rolling, as expected, the grains were further got elongated in RD and formed a heavily banded structure (figure 3(a) and 3(b)). Secondary electron SEM micrograph (figure 3(c)) shows the broken intermetallic particles after cold rolling. As the thickness of sheet reduced during cold rolling, non-uniformity of intermetallic particles increased and their sizes were in the range 6 µm to 10 µm. Cold rolling

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also increases the dislocation density in the material, which increases the stored energy within the material, which is the driving force for subsequent recrystallization. Figure 4 shows the BF-

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LOM, PLOM and secondary electron SEM images of the annealed sample. After annealing at 450ºC for 16 h, the banded structure was transformed into the near equiaxed structure (figure

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4(b)), while the shape of the intermetallic particles was also changed. Earlier, they had more

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elongated morphology. After annealing, there was particle coarsening, recrystallization and increase in the non-uniformity of size of intermetallic particles. Figure 5 shows the frequency

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distribution of the major axes of the intermetallic particles for various conditions. Coarse particles in size range 1-16 µm was observed. A large number of particles in size range 6 to 8 µm

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were observed in the annealed condition [32]. The intermetallics particles (second phase) after annealing had a higher amount of Fe, Si and Mn than that in as-cast condition as determined by EDS indicating the formation of stable α-Al12(Fe,Mn)3Si phase. Figure 6 shows the EBSD inverse pole figure (IPF) map of the as-cast, hot rolled, cold

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rolled, and annealed AA3003 alloy samples. The EBSD results supplement the BF-LOM, PLOM and SEM results. The changes in grain size during the process (hot rolling→cold rolling→annealing) can be understand through these EBSD maps. Initially, as-cast alloy had large grain structure with average grain size approximately 111 µm. After hot rolling and subsequent cold rolling, microstructure showed banded structure with lots of un-indexed points

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(possibly due to higher dislocation density and second phase particles). After annealing, fine, uniform and nearly equiaxed structure with approximately 22 µm average grain size was obtained. It is expected that the fine and uniform grain structure in annealed material will result in increased yield strength than as-cast material [33,34]. However, it needs to ne noted that the second phase particles may also play an important role and may not increase the strength. It

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remains to be tested. Table 2 shows the proportion of major elements and Fe:Si ratio in as-cast, hot rolled, cold rolled, and annealed condition. As-cast material showed precipitates with chinese

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script morphology with higher Fe:Si/10:1 ratio and lower content of Fe, Mn, and Si. The Fe:Si ratio decreased with processing, but did not showed any specific trend with the processing

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condition. Figure 7 shows the φ2=0º, 45º and 65° constant section of orientation distribution

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function (ODF) showing standard texture components that typically occurs in FCC metals and alloys. Figure 8 shows the φ2=0º, 45º and 65° constant section of ODF for as-cast and hot rolled

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sample, while figure 9 shows the φ2=0º, 45º and 65° constant section of ODF for cold rolled and annealed samples. As-cast sample showed the weak cube texture (figure 8(a)). After hot rolling

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(figure 8(b)), Brass, Cu, S and Goss increased in volume fraction, while cube decreased. The volume fraction of various texture fibers/components (in %) is given in Table 3. After cold rolling, Brass, Cu, S and Goss further increased in volume fraction i.e. strong deformation texture was developed. Annealed AA3003 alloy had weak Cu, S, Brass and Goss texture.

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Volume fraction of cube was also not changed significantly. The annealing texture consisted mainly of retained rolling texture components (i.e. Cu, S, Brass, Goss with some cube). After annealing, weakening of deformation texture was observed as recrystallization texture forms at the expense of rolling texture [19,20]. Goss and cube are considered metastable components and are reported to grow during recrystallization. Generally, Brass is the preferable nucleation site

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for Goss oriented [35] and Cube grains originate from deformed cube bands during annealing [21]. Although, in [36], it was suggested that for 8xxx series, after recrystallization, deformation texture decreased significantly, while cube increased. However, in this study, the improvement of cube during annealing was not observed. Usually, a deformed grain acts as a source for subsequent recrystallized nuclei and has nearly similar orientation as that of the deformed grain from which it originates. This phenomenon has been reported for recrystallization of cube in

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aluminium [7,37,38] and for recrystallization of -fiber (ND//<111> in low carbon steels [39–

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41]. The cube recrystallized grains are expected to be part of original cube in deformed microstructure. The cube orientation has lower stored energy [37,38,42] and presence of growth

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favorable 40°<111> boundaries [43]. During particle stimulated nucleation (PSN), nucleation

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occurs from the particle deformed zones due to large differences in the stored energy. These particle deformed zones and correspondingly PSN grains are of randomized nature [44]. This has

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also been observed in the present investigation, where PSN does not lead to improvement in the cube texture. The second phase particle plays an important role in the formation of β-fibre also

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[45–47] and affects the dislocation motion or slipping type, which further controlling the recrystallization texture by inhibiting the formation of Goss and cube grain as observed in this study.

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The nature of texture evolution in AA3003 is complex as second phase particles also playing an important role in texture evolution by controlling lattice rotation during rolling and annealing. The rolling texture is less stable and easy to rotate towards shear texture (r-Cube in FCC alloys) rather than forming Goss and cube {100}<100> because of activated slip system and shear stress [48–50]. For aluminium and its alloys used for deep drawing applications, special attention in given to the earing behavior of the can stock material. The amount of earing

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in can stock serves as accept or reject criterion in many cases. The control of earing requires a careful control of the texture. The deformation texture of cold rolled aluminium consists of Cu, S and Brass component. These components lead to the formation of 45° ears [51]. These 45° ears can be compensated by 90° ears. The 90° ears are formed due to cube component (which usually forms during recrystallization) in aluminium [51]. Hence a proper balance of deformation and

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recrystallization texture should be there in the final material (prior to deep drawing). The situation is very complex in commercial alloys like AA3003. However, it is generally accepted

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that cube oriented grains are nucleated in recrystallization during hot rolling at the persistent cube bands [52]. They are stabilized by high temperature non-octahedral slip on {110}<011> as

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suggested from single crystal studies [43]. At low temperature deformation, these cube grains are

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unstable and rotate away. Therefore, there should be sufficient amount of cube oriented grains in the hot rolled material. Some of these cube grains will persist through the cold rolling schedule

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and will act as potential nuclei for subsequent recrystallization process. In the final material, there should be perfect balance of rolling and recrystallization texture to achieve minimum

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earing. Large particles (>2.5-3μm) promote PSN and will decrease the recrystallized grain size with simultaneous increase in random texture components. This will also decrease the cube grains and will generate a weaker cube texture. The formation of large particles is usually reduced by reducing the Mn, Fe and Si content. In the present case, large Fe-Mn-Si precipitates

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are observed which results in the weakening of the cube texture. After annealing, Cube and Goss volume fraction were 1.5% and 3.5% respectively, while the deformation texture components like Brass, Copper, and S were 12.3%, 9.7%, and 19.2% respectively as given in Table 3.

4. Conclusions

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Based on the present investigation, following conclusion can be drawn: -

After hot rolling and cold rolling of as-cast material, large particles of intermetallic (mainly in the form of chinese script morphology consisting of Fe-Mn-Si) were broken into smaller particles with increased Fe, Mn, and Si content indicating the formation of αAl12(Fe, Mn)3Si phase. The initial as-cast AA3003 alloy had a very weak cube ({100}<100>) texture. After hot

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rolling and cold rolling, strong deformation texture consisting of Brass ({110}<112>),

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Cu ({112}<111>), S ({123}<634>), and Goss ({110}<011>) was developed. The cube

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component weakened.

After annealing at 450ºC for 16 hours, the deformation texture (Brass, Cu, S, and Goss)

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weakened, however, cube was also not improved. The as-cast material had very weak cube texture and due to particle stimulated nucleation (PSN) around large intermetallic

the present case.

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Author’s statement

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particles, a balance of deformation and recrystallization texture could not be achieved in

The authors declare that they do not have any competing financial interest or personal relationships that could have appeared to influence the work reported in this paper.

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Further, the work is novel and authors do not have any conflict of interest with anyone related to this work and amongst them.

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All the authors have contributed equally and significantly for the present work.

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Dr. Rajesh K. Khatirkar (Please consider it as my digital signature for this case only)

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Declaration of interests

The authors declare that they do not have any competing financial interest or personal relationships that could have appeared to influence the work reported in this paper.

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Further, the work is novel and authors do not have any conflict of interest with anyone related to this work and amongst them.

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Acknowledgment

The authors would like to thank The Director, VNIT Nagpur for providing necessary facilities

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for the present investigation and constant encouragement to publish this paper. The authors

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would also like to acknowledge the use of National Facility for Texture and OIM (A DST-

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IRPHA project), IIT, Bombay for EBSD and bulk texture measurements.

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List of Tables Table 1: Chemical composition (in weight % alloying elements) of AA3003 aluminium alloy used in the present investigation. Table 2: The chemical composition of major alloying elements present in precipitates (as determined by SEM-EDS) for as-cast, hot rolled, cold rolled and annealed samples. Table 3: Volume fraction (in %) of different texture components in as-cast, hot rolled, cold

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rolled, and annealed samples.

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List of Figures Figure 1: (a) Bright field light optical microscopy (BF-LOM), (b) polarized light optical microscopy (PLOM), (c) low magnification secondary electron scanning electron microscopy (SEM) and (d) high magnification secondary SEM images of as-cast AA3003 aluminium alloy sample. Figure 2: (a) BF-LOM, (b) PLOM and (c) secondary electron SEM images of hot rolled

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AA3003 aluminium alloy sample. Figure 3: (a) BF-LOM, (b) PLOM and (c) secondary electron SEM images of cold rolled

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AA3003 aluminium alloy sample.

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Figure 4: (a) BF-LOM, (b) PLOM and (c) secondary electron SEM images of annealed AA3003 aluminium alloy sample.

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Figure 5: Frequency distribution of major axes (in μm) of intermetallic particles for hot rolled, cold rolled and annealed samples. AC=as-cast, HR=hot rolled and CR=cold rolled.

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Figure 6: Electron backscattered diffraction (EBSD) inverse pole figure (IPF) maps of (a) ascast, (b) hot rolled, (c) cold rolled and (d) annealed samples.

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Figure 7: φ2=0°, 45°and 65° constant sections of orientation distribution function (ODF) showing standards components that typically occur in FCC metals and alloys. Figure 8: φ2=0°, 45° and 65° constant section of ODFs for (a) as-cast and (b) hot rolled samples. Contours: 2.0 3.0 4.0 5.0 6.0 8.0 10.0 12.0 14.0 16.0

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Figure 9: φ2 φ2=0°, 45° and 65° constant section of ODFs for (a) cold rolled and (b) annealed samples. Contours: 2.0 3.0 4.0 5.0 6.0 8.0 10.0 12.0 14.0 16.0

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Figure 6

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Table 1: Chemical composition (in weight % alloying elements) of AA3003 aluminium alloy used in the present investigation.

Alloy AA3003

Si 0.4

Fe 0.65

Cu 0.1

Mn 1.2

Zn 0.10

Al Balance

Table 2: The chemical composition of major alloying elements present in precipitates (as

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determined by SEM-EDS) for as-cast, hot rolled, cold rolled and annealed samples.

As-cast

4.

Fe:Si

6.5

0.6

1.2

10

Needle

44.6

26.4

6.0

3.9

4

46.4

24.6

6.3

6.1

4

49.5

26.1

3.3

1.1

8

Circular

80.6

9.2

0.0

2.9

9

As-cast + Hot rolled + Cold rolled

Rectangular

64.3

17.6

2.7

3.4

6

Square

78.7

9.2

1.3

1.2

7

Circular

96.4

0.7

0.2

0.7

4

As-cast + Hot rolled +

Rectangular

49.8

23.2

5.2

8.9

4

Needle

55.6

22.8

4.2

4.1

5

As-cast + Hot rolled

Rectangular

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3.

Mn

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Condition

Morphology of Composition (weight %) the intermetallic Al Fe Si particles

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Sr. No.

Triangular

31

Cold rolled + Annealed

Circular

97

0.9

0.2

1.1

4

Triangular

58.7

20.2

4.2

3.9

5

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Table 3: Volume fraction (in %) of different texture components in as-cast, hot rolled, cold

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rolled, and annealed samples.

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S

Cube

2.5

8.3

3.5

12.1

5.9

19.0

1.9

15.9

6.8

28.3

1.7

9.7

3.5

19.2

1.5

Condition

Brass

Cu

1.

As-cast

5.5

5.1

2.

Hot rolled

12.8

3.

Cold rolled

15.0

4.

Annealed

12.3

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Sr. No.

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