Effect of heating rate on mechanical property, microstructure andtexture evolution of AlMgSiCu alloy during solution treatment

Xiaofeng Wang, Mingxing Guo n, Lingyong Cao, Jinru Luo, Jishan Zhang, Linzhong ZhuangState Key Laboratory for Advanced Metals and Materials, University of Science and Technology Beijing, Beijing 100083, China

a r t i c l e i n f o

Article history:Received 19 August 2014Received in revised form11 October 2014Accepted 17 October 2014Available online 28 October 2014

Keywords:AlMgSiCu alloyHeating rateMechanical propertyAnisotropyRecrystallization texture

a b s t r a c t

The effect of heating rate on the mechanical properties, microstructure and texture of AlMgSiCu alloyduring solution treatment was investigated through tensile testing, scanning electron microscope,scanning transmission electron microscope, metallographic observation and EBSD measurement.The experimental results reveal that there are great differences in the mechanical properties, micro-structures and textures after the solution treatment with two different heating rates. Compared with thealloy sheet solution treated with slow heating rate, the alloy sheet solution treated with rapid heatingrate possesses weak mechanical property anisotropy and higher average r value. The equiaxed grain isthe main recrystallization microstructure for the case of rapid heating rate, while the elongated grainappears in the case of slow heating rate. The texture components are also quite different in the twocases, CubeND orientation is the main texture component for the former case, while the latter oneincludes Cube, R, Goss, P and Brass orientations. The relationship between r value, texture componentsand microstructure has also been established in this paper.

& 2014 Elsevier B.V. All rights reserved.

1. Introduction

There is an increasing demand for the use of age hardenableAlMgSiCu alloy within the automotive industry, due to itsadvantages of high strength-to-weight ratio, good corrosion resis-tance and formability [16]. The typical thermomechanical pro-cessing of AlMgSiCu alloy used as car body sheet mainlyconsists of casting, scalping, homogenization, hot rolling, inter-mediate annealing, cold rolling, solution treatment, pre-aging,natural aging, forming, painting and paint baking [6]. Since nalrecrystallization texture and microstructure developed duringsolution treatment play a critical role in controlling the mechanicalproperty anisotropy and the deep drawability, it is very importantto optimize them to reduce the mechanical property anisotropyand improve the deep drawability. Accordingly, it is very necessaryto consider the effect of solution treatment on recrystallizationmicrostructure and texture.

Two major annealing processes for cold-rolled sheets arecontinuous annealing and batch annealing. The main differencebetween them is the heating rate. The heating rate of the formercase is fast and that of the latter case is slow. This may result indifferent precipitations during the different recrystallization

processes. Humphreys et al. [7] suggested that the recrystallizationbehavior during annealing can be divided into three cases: the rstcase is that precipitation takes place before recrystallization,the second case is that precipitation and recrystallization occurconcurrently, the last case is that recrystallization takes placebefore precipitation. Accordingly, the heating rate should play animportant role in the precipitation and recrystallization.

Some studies on the inuence of heating rate on the micro-structure and texture of materials have been carried out recently[810]. It has been found that an increase of heating rate has littleeffect on the nal grain size in the particle-containing alloy, butcan result in an increase in nal grain size for the single-phasealloy. In addition, according to the study on the effect of heatingrate on the microstructure and texture of continuously castAA3105 aluminum alloy, Liu et al. revealed that the recrystalliza-tion texture is characterized by relatively strong P orientation and22.51 ND rotated cube orientation in the case of slow annealing,and the elongated grain is the main microstructure, while only theweak cube orientation is formed in the case of rapid annealing,and the size and morphology of recrystallized grains greatlydepend on the annealing conditions, especially for the annealingtemperature. However, the effect of solution heating rate on themechanical property, texture and microstructure of AlMgSiCualloy is still unclear, and because with the change of heating rate,the precipitation and dissolution of the secondary phases, andrecrystallization process during the solution treatments all change

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Materials Science & Engineering A

http://dx.doi.org/10.1016/j.msea.2014.10.0450921-5093/& 2014 Elsevier B.V. All rights reserved.

n Corresponding author: Tel.: 86 10 82375844.E-mail address: mingxingguo@skl.ustb.edu.cn (M. Guo).

Materials Science & Engineering A 621 (2015) 817

greatly, their changes can further have an inuence on the nalmicrostructure and mechanical properties of the alloy sheet. Thus,it is quite necessary to establish the relationship between thesolution heating rate, mechanical properties, microstructure andtexture of AlMgSiCu alloys. Accordingly, the aim of this paperis to study the effect of heating rate on the mechanical properties,microstructure and texture of AlMgSiCu alloy, and hopefullyprovide a guide for the optimization of their thermomechanicalprocessing.

2. Experimental

The material used in the present research was a cold-rolledAlMgSiCu series alloy sheet with a thickness of 1 mm. Thechemical composition of the alloy is Al0.8 Mg0.9Si0.5Cu0.2Fe0.1Mn (wt%). The sheet was divided into two parts. Onepart of the sheet denoted as A was solution treated at 555 oC for2 min in a salt bath furnace with a heating rate of 60 oC/s and theother part of the sheet denoted as B was also solution treated atthe same temperature for the same holding time in an air furnacewith the heating rate of 1 oC/min, as shown in Fig. 1. It is worthnoting that in order to clearly understand the differences in theprecipitation, solution and recrystallization during solution treat-ments with the different heating rates, three cold-rolled sampleswere heated up from room temperature to 300 oC, 350 oC and400 oC with a heating rate of 1 oC/min, respectively, and then theywere taken out from the air furnace and quenched in cold water(intermediate processes of the slow solution treatment), whileanother two cold-rolled samples were directly put into the saltbath furnace with a temperature of 555 oC, and solution treated atthis temperature for 10 and 15 s, respectively (intermediateprocesses of the rapid solution treatment). After the solutiontreatments, both the parts were pre-aged at 80 oC for 12 h rstand then naturally aged for 14 days (T4P treatment).

The mechanical properties of the T4P treated sheets, includingyield strength (YS), ultimate tensile strength (UTS), elongation,n and r values, were investigated at room temperature in the threedirections of 01, 451 and 901 with respect to the rolling directionusing MTS810 testing machine. Among the above parameters,r value was determined by a tensile strain of 15%.

The microstructure of the alloy sheets in different conditionswas characterized by Carl. ZEISS Axio Imager A2m optical micro-scope. The polished samples were etched by Keller reagent.Analysis on large particles distributed in the samples and fracturemorphology of the tensile test samples was conducted througha SUPRA 55 scanning electron microscope (SEM) equipped with

X-ray energy dispersive spectrometer (EDS) systems. The through-thickness recrystallization microstructures and textures of thesolution treated samples were characterized by electron back-scatter diffraction (EBSD) analysis on a SUPRA 55 scanningelectron microscope. EBSD samples were prepared by standardmechanical grinding and electrolytic polishing. In accordance withthe grain size, the step size of 3 m was applied. The grainstructure and texture were analyzed by HKL Channel 5 software.Orientation distribution functions (ODFs) were calculated by theharmonic series expansion method (orthorhombic sample sym-metry, lmax22, Gaussian spread51).

The size and distribution of particles of the solution treatedsamples were investigated through a Tecnai G2 F30 transmissionelectron microscope (TEM) equipped with a high angle angulardark eld (HAADF) detector and X-ray energy dispersive spectro-meter (EDS) systems. TEM samples were mechanically polished toapproximately 100 m and then twin-jet polished in an electrolytecontaining 30% nitric acid and 70% methanol at a temperature of25 1C.

3. Results

3.1. Mechanical properties characterization

Fig. 2 shows the stressstrain curves of the two T4P treatedalloy sheets. It can be clearly seen that their mechanical propertiesare different in three directions. The detailed mechanical proper-ties of the two T4P treated sheets in the three different directionsare summarized in Table 1. The results reveal that the mechanicalproperty anisotropy in sheet A is weak, and the elongation in the901 direction is a little lower than that of the other two directions.But the mechanical property anisotropy is increased in sheet B,especially for the elongation. The elongation in the 901 direction isdecreased much more as shown in Fig. 2. The lower elongationshould be resulted from the elongated grains formed by the slowheating solution treatment as shown in the following part. Inaddition, LDR (limiting drawing ratio) value is usually used toevaluate deep drawability. Leu [11] pointed out that LDR valuedepends on both r and n values, and can normally be expressed asfollows:

LDR

exp 2f exp n

1r

2

r" #exp 2n

1r

2

r" #1

vuut ;where f is the factor of drawing efciency, and when f equals

0.9, the calculated results are in good agreement with the

Fig. 1. Solution treatment curves of different processes (a) salt bath furnace and (b) air furnace.

X. Wang et al. / Materials Science & Engineering A 621 (2015) 817 9

experimental results [12]. Based on the equation, the LDR values ofsheets A and B are 2.01 and 1.99, respectively. This result revealsthat the deep drawability of sheet A is somewhat higher than thatof sheet B.

3.2. Fracture morphologies of the two T4P treated tensile testsamples

The typical SEM micrographs of the fracture morphology aftertension are shown in Fig. 3. Although many dimples can beobserved in 01 and 901 directions for sheet A and sheet B, yet,the dimples in the 01 direction for two alloy sheets are muchsmaller and deeper than those in the 901 direction, indicating thatthe two alloy sheets in the 01 direction have better ductility. Thisfracture morphology well agrees with the elongation results asshown in Table 1. Because the mechanical property anisotropy isstrongly inuenced by texture, grain shape, grain size and theprecipitates developed during aging, it is essential to analyze thedifferences in the microstructure and texture of sheet A andsheet B.

3.3. Through-thickness recrystallization microstructurecharacterization

Fig. 4 shows the through-thickness recrystallization micro-structures of the two solution treated sheets. Sheet A is comprisedof equiaxed grains, while sheet B is comprised of elongated grains.Some black un-dissolved constituent particles, such as AlFeMnSi(detailed analysis on them as shown in the following parts), tendto align along the rolling direction. The different grain structurescan be clearly seen in Fig. 5(a) and (b). According to statisticscalculation, the average grain aspect ratio (about 6:5) in sheet A ismuch lower than that (about 5:2) in the alloy sheet B. Fig. 5(c)and (d) shows the grain size distributions of the two alloy sheets.It can be found that the grain size distribution of sheet A is more

uniform than that of sheet B. It seems that solution heating ratehas a great inuence on the grain structure. The different grainstructure further has an effect on the mechanical property aniso-tropy and the deep drawability. Cho et al. [13] have conrmed thatan equiaxed grain should be benecial to reduce mechanicalproperty anisotropy.

3.4. Through-thickness recrystallization texture characterization

The through-thickness textures of the two sheets are shown inFig. 6. It can be found that they have different texture components.Sheet A mainly consists of CubeND {001} 310 orientation, whilesheet B contains Cube {001} 100, Goss {110} 001, P {011} 122,R {124} 211 and Brass {011} 211 orientations. The deformationtextureBrass orientation should be developed during the cold-rolling process, and still retained after solution treatment.The spatial distribution of grains within 151 of their exact orienta-tions is shown in Fig. 5. The grain color will gradually fade with theincrease of angle deviation from the exact orientation. It can alsobe found that the weak texture was developed through rapidheating during solution treatment. The intensities and volumefractions of the specic texture components in the two sheets arelisted in Table 2. Based on the texture results, it seems that heatingrate also has a signicant inuence on the development of texturecomponents and intensities.

3.5. Precipitation and microstructure evolution

As discussed above, there is a signicant difference in themechanical properties, microstructures and texture components inthe samples solution treated with rapid and slow heating rates;it is necessary to study their precipitations and microstructuresevolution during the solution treatment or heating process.

The distributions of precipitates in the alloy matrix beforesolution treatment are shown in Fig. 7(a) and (b). It can be found

Fig. 2. Engineering stressstrain curves of the T4P treated sheets in different directions (a) sheet A and (b) sheet B.

Table 1Mechanical properties of the two T4P treated samples.

AlMgSi Direction (deg) r Average r r n Average n Elongation (%) YS (MPa) UTS (MPa)

A 0 0.649 0.62 0.007 0.309 0.308 26.4 145 28845 0.623 0.308 26.7 138 27690 0.584 0.307 26 141 280

B 0 0.579 0.569 0.082 0.303 0.308 26.6 154 29345 0.528 0.308 26.9 137 27390 0.641 0.314 25.6 136 278

X. Wang et al. / Materials Science & Engineering A 621 (2015) 81710

that a bimodal particle distribution has been formed beforesolution treatment. A large number of white coarse particles hasa spatial density of 103 mm2, and a larger number of black neparticles has a spatial density of 1.5104 mm2. According to theEDS analysis, the white and black particles are identied as Al(Fe,Mn)Si and Mg2Si, respectively (as shown in Fig. 7(c) and (d)).The size of the coarse particles is in the range of 1.225 m and theaverage size of the ne particles is about 750 nm. Fig. 8(a) showsBF (bright eld) image of the cold-rolling band, a high density ofdislocations, and dislocation cells can be observed in the alloymatrix. Two types of particles can be observed in Fig. 8(b). Thecorresponding selected area diffraction (SAD) analysis is givenin Fig. 8(c) and (d). The type of small particles with a size of120300 nm, attributed to the broken of large Al(Fe, Mn)Si particlesduring the rolling process, is identied as -Al19Fe4MnSi2 withbody-centered cubic structure. The observed -Al19Fe4MnSi2 parti-cles normally cannot be dissolved during the solution treatment.

The type of lath-shaped particles with an average size of 650 nm isidentied as Q (Al1.9Mg4.1Si3.3Cu) with the hexagonal structure.They normally can be dissolved during the solution treatment.

With the increase of solution time, the microstructures evolu-tion of the samples solution treated at 555 1C with rapid heatingrate is shown in Fig. 9. The microstructure of the sample solutiontreated for 10 s is comprised of some slightly elongated andequiaxed grains, and the fraction of recrystallization grains isdominated, indicating that the recrystallization has alreadyoccurred. With increasing the time to 15 s, the equiaxed grainsbecome the main microstructure as shown in Fig. 9(b), indicatingthat the recrystallization basically has been nished. According tothe above results, the speed of recrystallization is very fast andmay be faster than that of precipitates dissolution rate (2 min areneeded for the complete solution treatment).

The microstructures evolution of the solution treated sampleswith slow heating rate is shown in Fig. 10. The microstructure of

Fig. 3. Fracture morphology of T4P treated tensile test sheets in different directions. (a) 01 of sheet A, (b) 901 of sheet A, (c) 01 of sheet B and (d) 901 of sheet B.

Fig. 4. Through-thickness recrystallization microstructure of solution treated alloy sheets (a) sheet A and (b) sheet B.

X. Wang et al. / Materials Science & Engineering A 621 (2015) 817 11

Fig. 5. EBSD maps of the solution treated alloy sheets (a) grain microstructure of sheet A, (b) grain microstructure of sheet B, (c) grain size distribution of sheet A and(d) grain distribution of sheet B. The grain orientations are presented as: aqua, CubeND; red, Cube; green, R; blue, P and yellow, Brass. (For interpretation of the references tocolor in this gure legend, the reader is referred to the web version of this article.)

Fig. 6. Through-thickness recrystallization textures of the solution treated alloy sheets (a) sheet A and (b) sheet B.

X. Wang et al. / Materials Science & Engineering A 621 (2015) 81712

the samples heated up to 300 1C or 350 1C is comprised of highlyelongated bands, and the recrystallization grains still cannot beobserved in the alloy matrix. In order to understand the change inthe number density of Mg2Si particles during the slow heatingprocess, the number density of Mg2Si particles in the samplesheated up to different temperatures was analyzed by SEM andSTEM as shown in Figs. 11 and 12. Compared with the cold-rolledsample, the number density in the two samples was increasedgreatly as shown in Fig. 11. And lots of ne particles can be clearlyseen in Fig. 12(a) and (b). And EDS analysis results show that theparticles are mainly comprised of Q (Al1.9Mg4.1Si3.3Cu) and-Al19Fe4MnSi2 as shown in Fig. 13(c) and (d). Their spatialdensities are 5105 mm2 at 300 1C and 106 mm2 at 350 1C,respectively, indicating that the number density of the precipitateshas a slight increase with the increase of temperature. Addition-ally, their sizes are basically in the range of 150600 nm. There-fore, it can be found that there is a heavy precipitation during theheating up process. The formed precipitates not only grow duringthe heating up process, but can also retard the further growth ofthe recrystallization grains. When the temperature is heated up to400 1C, the sample is comprised of coarse elongated grains,indicating that the recrystallization has almost nished. This canbe further conrmed by the very low number density of disloca-tions in the alloy matrix as shown in Fig. 13.

Based on the above results, it can be concluded that solutionheating rate can affect precipitation and microstructure evolutionsignicantly, which would further affect the texture componentsin the alloy matrix.

4. Discussion

4.1. The effect of heating rate on microstructure

The experimental results have revealed that the heating ratehas a signicant inuence on the microstructure and properties ofAlMgSi series alloy. A similar phenomenon has been observed inAA3015, AlMn and AlMnMg alloys [10,14,15], which can beattributed to the effect of concurrent precipitation on recrystalli-zation behavior. In the present alloy, the driving force for recrys-tallization can be expressed as [7,8]

V MP MnPDPCPZ M0 exp Q=kT Gb2

22b

R3FVb

dP

!1

where M, PD, PC and PZ are the mobility of grain boundaries, thestored energy of deformation, the retarding pressure due to thegrain boundary curvature and the Zener drag, respectively. Q, T, ,G, b, R, FV, dP represent the activation energy, the temperature, thedislocation density, the shear module, the boundary energy, thegrain radius, the volume fraction and diameter of the smallparticles (o1 m), respectively.

The difference in the microstructure between the alloy sheetssolution treated with slow and rapid heating rates can be explained asfollows. On one hand, the driving force for recrystallization of samplesolution treated with rapid heating rate is higher than that of samplesolution treated with slow heating rate, because the stored energy isconsumed much more before the occurrence of recrystallization.On the other hand, lots of ner precipitates can be formed duringthe heating up process with the slow heating rate, and then theformed small particles would give a signicant retard force on themovement of grain boundaries along ND, and the occurrence ofrecrystallization, thus, the elongated grains can be observed in thesample solution treated with the slow heating rate.

4.2. The effect of heating rate on texture

It has been repeatedly stated that the recrystallization behaviorof particle-containing Al alloys is further inuenced by the

Table 2The volume fractions of recrystallization texture components in the two samples.

Sheet Component Intensity Volume fraction (%)

A CubeND 3.78 11Cube 5.18 6.02Goss 2.06 3.41

B P 1.65 4.15R 2.21 13.9Brass 2.6 5.27

Fig. 7. SEM micrographs of the cold-rolling alloy sheet. (a, b) Morphology of the particles and (c, d) EDS spectra of white and black particles.

X. Wang et al. / Materials Science & Engineering A 621 (2015) 817 13

precipitation state, and this can result in different recrystallizationtextures [16,17]: large particles with sizes larger than 1 m canpromote recrystallization as a result of the particle stimulated nuclea-tion (PSN) effect and tend to weaken texture, or only develop thetexture components, i.e., CubeND and P orientations, while smallparticles with sizes below 1 m can impede the movement of grain

boundaries, and further result in the formation of Cube, CubeRD(resulting from the recrystallization grain nucleation at the so calledcube band). R, Q {013}231 and Goss orientations are determined bythe nucleation sites such as shear bands or grain boundaries.

It has been stated that the present AlMgSi alloy contains abimodal particle distribution, thus the texture should be inuenced by

Fig. 8. The particles and their SADPs in the cold-rolling alloy sheet (a) BF image, (b) STEM image, (c) [001] SADP from -Al19Fe4MnSiz and (d) [120] SADP fromQ (Al19Mg4.1Si3.3Cu).

Fig. 9. Microstructure of rapid heating sample solution treated at 555 1C for different times (a) 10 s and (b) 15 s.

X. Wang et al. / Materials Science & Engineering A 621 (2015) 81714

a combination of large and small particles together. Some researchershave [16,18] pointed out that the recrystallization texture is deter-mined by the competition between PSN effect and nucleation at cubebands. The critical particle size for the growth of a nucleus to initiatePSN effect can be expressed as [19,20]

dcrit 4b

PDPZ 4b

Gb2=2

3FV b=dp 2

where b, PD and PZ are the specic grain boundary energy, thedeformation stored energy and the Zener pinning force exerted by thesmall particle, respectively. FV and dp are the small particle volumefraction and diameter, respectively.

From Eq. (2), the critical particle size increases with increasingPZ, which is strongly inuenced by the volume fraction and sizes ofsmall particles. In other words, their volume fraction and sizeshave a signicant effect on the evolution of recrystallizationtexture. According to Engler's results [6], even a mixture of cubeand PSN recrystallization texture can be obtained through con-trolling the volume fraction and sizes of small particles. Thus, it ispossible to optimize the texture components by controlling theprecipitation state. According to the results shown above, we canalso nd that it is easier to develop CubeND orientation throughPSN effect as a result of the relatively few small particles in thesample solution treated with a rapid heating rate, while in thesample solution treated with a slow heating rate, it is easier to

Fig. 10. Microstructure of the alloys heated up to different temperatures with a slow heating rate (a) 300 1C, (b) 350 1C and (c) 400 1C.

Fig. 11. SEM micrographs of the alloys heated up to different temperatures with a slow heating rate (a) 300 1C and (b) 350 1C.

X. Wang et al. / Materials Science & Engineering A 621 (2015) 817 15

develop Cube, R, Goss and P orientations. The appearance of Porientation suggests that PSN also have an effect on the textureevolution during the slow heating up process.

4.3. The effect of texture and grain morphology on the deepdrawability

It is well known that the deep drawability can be characterizedby the average r value and r value which are strongly affected bythe texture components. Different texture components correspondto the different average r and r values. The simulated average rand r values of some specic texture components are summar-ized in Table 3. Liu [21] reported that the CubeND component,corresponding to the average r40.5 and ro1, is more benecialto improve the deep drawability than that of Cube orientation.

The r values of samples A and B can be calculated by thefollowing equation [21]:

rVjrj 3

Fig. 12. The distribution of particles in the alloys heated up to different temperatures with a slow heating rate (a) 300 1C, (b) 350 1C, (c) EDS spectra of particle A and (d) EDSspectra of particle B.

Fig. 13. TEM micrograph of the alloy heated up to a temperature of 400 1C.

Table 3Values of average r and r for some texture components.

Designation Miller indices {hkl}uvw Average r r

Cube {001}100 0.5 1Goss {110}001 15 30R {124}211 1.9 1.2P {011}122 2.8 1.6Brass {011}211 4.7 8.1

X. Wang et al. / Materials Science & Engineering A 621 (2015) 81716

where rj is the r value of single crystal in the j-th orientationand Vj is the volume fraction of the j-th orientation.

According to Eq. (3) and the texture components as shown inTable 2, sample A should possess a lower r value and a loweraverage r value. However, the experimental results reveal thatsample A possesses lower r value and higher average r value.Chung et al. [13,22] suggested that grain morphology also has aneffect on the mechanical property anisotropy. The equaixed grainsnormally correspond to the lower r value, while the elongatedgrains normally increase the r value. Delannay et al. [23] havealso found that the equaixed grains are favorable to increase theaverage r value by some simulation works. Considering thecombination effects of texture and grain morphology on the rand r values, the observed higher r value in sample A should beattributed to the equaixed grains although the texture compo-nentCube orientation corresponds to the lower r value. Therefore,the deep drawability should be improved by controlling texturecomponents and microstructure, especially the grain morphology.

5. Conclusions

The effect of heating rate on the mechanical properties, micro-structure and texture of the AlMgSiCu alloy during solutiontreatment was investigated. The conclusions are as follows:

(1) The mechanical property anisotropy of the alloys in the T4Pcondition is affected by the heating rate of solution treatment.Compared with the slowly heated sample, the fast heatedsample possesses a weak mechanical property anisotropy andhigher average r value.

(2) The recrystallization microstructure of the alloys is greatlyinuenced by the heating rate. The fast heated sample iscomprised of almost equiaxed grains with a more uniformsize, while the slowly heated sample is comprised of elongatedgrains with a high length/width ratio.

(3) The recrystallization texture of the alloys is also signicantlyaffected by the applied heating rate during solution treatment.In the case of fast heating, the texture component mainlyconsists of CubeND orientation, while in the case of slowheating, the texture is characterized by Cube, P, R, Goss andretained Brass orientations.

(4) The mechanical property anisotropy of the alloys, especially rvalue, not only depends on the texture components but alsoon the grain morphology. The ne equiaxed grains are morefavorable to increasing r value of the alloy sheet.

Acknowledgments

This work was supported by National High Technical Researchand Development Program of China (No. 2013AA032403), BeijingHigher Education Yong Elite Teacher Project in 2013 (YETP0409)and National Natural Science Foundation of China (No. 51301016).

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X. Wang et al. / Materials Science & Engineering A 621 (2015) 817 17

Effect of heating rate on mechanical property, microstructure and texture evolution of AlMgSiCu alloy during solution...IntroductionExperimentalResultsMechanical properties characterizationFracture morphologies of the two T4P treated tensile test samplesThrough-thickness recrystallization microstructure characterizationThrough-thickness recrystallization texture characterizationPrecipitation and microstructure evolution

DiscussionThe effect of heating rate on microstructureThe effect of heating rate on textureThe effect of texture and grain morphology on the deep drawability

ConclusionsAcknowledgmentsReferences