Recrystallization Texture Competition Mediated by Segregation Element in Body-Centered Cubic Metals

doi:10.11900/0412.1961.2023.00077

Acta Metall Sin

2023, Vol. 59

Issue (8): 1065-1074 DOI: 10.11900/0412.1961.2023.00077

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Recrystallization Texture Competition Mediated by Segregation Element in Body-Centered Cubic Metals

CHANG Songtao¹, ZHANG Fang¹, SHA Yuhui¹, ZUO Liang¹^,²(

)

¹Key Laboratory for Anisotropy and Texture of Materials, Ministry of Education, Northeastern University, Shenyang 110819, China
²Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China

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CHANG Songtao, ZHANG Fang, SHA Yuhui, ZUO Liang. Recrystallization Texture Competition Mediated by Segregation Element in Body-Centered Cubic Metals. Acta Metall Sin, 2023, 59(8): 1065-1074.

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Abstract

Recrystallization texture is determined by the competition among various texture components during nucleation and grain growth. The stored energy and orientation gradient depend on the grain orientation in the deformed microstructure. Texture components, nucleating at positions with high stored energy and a sharp orientation gradient have kinetic advantages, can consume the nucleation sites and potential growth space of recrystallized grains in adjacent deformed grains. Segregation elements can hinder nucleation and growth of recrystallization grains by reducing grain boundary mobility, and thus prevent texture components with kinetic advantages from invading adjacent deformed grains. It is valuable to provide a basis for precise recrystallization texture design and control by investigating the competitive relations among recrystallization texture components under the intervention of segregation elements. The recrystallization texture competition in a body-centered cubic Fe-3%Si alloy containing Sb was studied through experiment and simulation. It was found that the segregation element can weaken the γ (<111>//ND, ND—normal direction) and strengthen the α (<110>//RD, RD—rolling direction), as well as other recrystallization texture components with low stored energy, by inhibiting the invasion of γ-recrystallized grains into adjacent deformed grains. The two dominant factors for segregation effects are deformation texture and critical invasion radius. A quantitative model, based on nucleation and growth kinetics, was proposed to explore the effect of critical invasion radius and deformation texture on recrystallization texture competition mediated by segregation elements. It was found that segregation elements can prolong the invasion incubation period and reduce the invasion rate to inhibit the consumption of α-deformed grains by γ-recrystallized grains. The inhibition effect initially strengthened and then weakened with the increasing γ deformation texture.

Key words: recrystallization texture grain boundary segregation body-centered cubic metal Fe-3%Si alloy

Received: 27 February 2023

ZTFLH:

TG142.77

Fund: National Natural Science Foundation of China(51931002)

Corresponding Authors: ZUO Liang, professor, Tel:(024)83691560, E-mail: lzuo@mail.neu.edu.cn

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https://www.ams.org.cn/EN/10.11900/0412.1961.2023.00077 OR https://www.ams.org.cn/EN/Y2023/V59/I8/1065

Fig.1 Constant φ₂ = 0° and 45° sections of ODFs at subsurface (S = 0.5) and center (S = 0) layers in cold rolled Fe-3%Si sheets without (a) and with (b) Sb addition (ODF—orientation distribution function; φ₁, φ₂, Φ—Euler angles; S—thickness parameter)

Fig.2 Constant φ₂ = 0° and 45° sections of ODFs at subsurface and center layers in recrystallized Fe-3%Si sheets without (a) and with (b) Sb addition

Fig.3 Difference of ODFs in constant φ₂ = 0° and 45° sections at subsurface (a) and center (b) layer in Fe-3%Si recrystallized sheets between without and with Sb addition

Fig.4 EBSD orientation image maps (a, c) and GND density maps (b, d) in cold rolled Fe-3%Si sheets without (a, b) and with (c, d) Sb addition (GND—geometrically necessary dislocation, ND—normal direction, RD—rolling direction)

Fig.5 EBSD orientation image maps in partially (a, c) and just completely recrystallized (b, d) Fe-3%Si sheets without (a, b) and with (c, d) Sb addition (Grain boundaries of deformed grains are represented by white dotted lines. A₁ and A₂ indicate α deformed regions before recrystallization. B₁, B₂, C₁, and C₂ indicate γ deformed regions before recrystallization)

Fig.6 EBSD orientation image maps of early (a, c) and middle (b, d) recrystallization stages without (a, b) and with (c, d) Sb addition (Grain boundaries of deformed grains are represented by white dotted lines. Invading and non-invading γ recrystallized grains are indicated by black and white arrows, respectively)

Fig.7 Schematics for the invasion process of γ recrystallized grains into adjacent α deformed grains
(a) γ grain nucleation
(b) γ recrystallized grain invasion into α defor-med grains (L—grain size, R_c—critical invasion radius)

Parameter	Value	Unit	Ref.
Temperature, T	1123	K
Shear modulus, G	87.88 - 0.02467T	GPa	[30]
Boltzmann's constant, k_b	1.38 × 10^-23	J·K^-1
Burgers vector modulus, b	0.25 × 10^-9	m	[30]
Mobility of free grain boundary, $M f r e e g b$	$9 × 10 - 8 e x p (- 1.99 × 10 - 19 k b T)$	m⁴·J^-1·s^-1	[31]
Mobility of free sub-grain boundary, $M f r e e s u b$	0.2 $M f r e e g b$	m⁴·J^-1·s^-1	[23]
Grain boundary width, δ^gb	1 × 10^-9	m	[26]
Sub-grain boundary width, δ^sub	δ^gb	m	This work
Number of atoms per unit volume, N_V	8.45 × 10²⁸	m^-3
Binding energy of Sb to sub-grain boundary, $E s e g s u b$	-0.43	eV	[32,33]
Binding energy of Sb to grain boundary, $E s e g g b$	-0.67	eV	[34]
Sb bulk diffusion coefficient, D_B	$1.3 × 10 - 5 e x p (- 3.37 × 10 - 19 k b T)$	m²·s^-1	[35]
Sb cross grain boundary diffusion coefficient, $D C g b$	2D_B	m²·s^-1	[26]
Sb cross sub-grain boundary diffusion coefficient, $D C s u b$	$D C g b$	m²·s^-1	This work

Table 1 List of parameters for simulating recrystallization behavior of Fe-3%Si alloy^{[23,26,30-35]}

Fig.8 Volume fraction of γ recrystallized grains invading into α deformed grains ( $X γ α / γ$ ) as a function of R_c without and with Sb addition (Δ $X γ α / γ$ —the inhibition effect of segregation element on invasion behavior)

Fig.9 Volume fraction of γ recrystallization texture invading into α deformed grains as a function of γ deformation texture fraction

Fig.10 Recrystallization kinetics at grain boundary region of α deformed grains ( $B α / γ$ —area fraction of recrystallized grain in the grain boundary of α-deformed grain, $B γ α / γ$ —area fraction of γ-recrystallized grain in the grain boundary of α-deformed grain, $B α α / γ$ —area fraction of α-recrystallized grain in the grain boundary of α-deformed grain)

1	Wauthier-Monnin A, Chauveau T, Castelnau O, et al. The evolution with strain of the stored energy in different texture components of cold-rolled IF steel revealed by high resolution X-ray diffraction [J]. Mater. Charact., 2015, 104: 31 doi: 10.1016/j.matchar.2015.04.005
2	Hawezy D, Birosca S. Disparity in recrystallization of α- & γ-fibers and its impact on cube texture formation in non-oriented electrical steel [J]. Acta Mater., 2021, 216: 117141 doi: 10.1016/j.actamat.2021.117141
3	Sanjari M, He Y L, Hilinski E J, et al. Texture evolution during skew cold rolling and annealing of a non-oriented electrical steel containing 0.9wt% silicon [J]. J. Mater. Sci., 2017, 52: 3281 doi: 10.1007/s10853-016-0616-y
4	Sebald R, Gottstein G. Modeling of recrystallization textures: Interaction of nucleation and growth [J]. Acta Mater., 2002, 50: 1587 doi: 10.1016/S1359-6454(02)00020-4
5	Fu Q, Sha Y H, Zhang F, et al. Correlative effect of critical parameters for η recrystallization texture development in rolled Fe₈₁Ga₁₉ sheet: Modeling and experiment [J]. Acta Mater., 2019, 167: 167 doi: 10.1016/j.actamat.2019.01.043
6	Sánchez-Araiza M, Godet S, Jacques P J, et al. Texture evolution during the recrystallization of a warm-rolled low-carbon steel [J]. Acta Mater., 2006, 54: 3085 doi: 10.1016/j.actamat.2006.02.050
7	Okuda K, Rollett A D. Monte Carlo simulation of elongated recrystallized grains in steels [J]. Comput. Mater. Sci., 2005, 34: 264 doi: 10.1016/j.commatsci.2005.01.013
8	Shimanaka H, Irie T, Matsumura K, et al. A new non-oriented Si-steel with texture of {100}<ovw> [J]. J. Magn. Magn. Mater., 1980, 19: 63 doi: 10.1016/0304-8853(80)90554-5
9	Vodopivec F, Marinšek F, Grešovnik F, et al. Effect of antimony of energy losses in non-oriented 1.8 Si, 0.3 Al electrical sheets [J]. J. Magn. Magn. Mater., 1991, 97: 281 doi: 10.1016/0304-8853(91)90192-D
10	Lee S, De Cooman B C. Effect of phosphorus on the magnetic losses of non-oriented 2%Si steel [J]. ISIJ Int., 2012, 52: 1162 doi: 10.2355/isijinternational.52.1162
11	Godec M, Jenko M, Mast R, et al. Texture measurements on electrical steels alloyed with tin [J]. Vacuum, 2001, 61: 151 doi: 10.1016/S0042-207X(00)00472-3
12	Chang S K, Huang W Y. Texture effect on magnetic properties by alloying specific elements in non-grain oriented silicon steels [J]. ISIJ Int., 2005, 45: 918 doi: 10.2355/isijinternational.45.918
13	Mavrikakis N, Saikaly W, Calvillo P R, et al. How Sn addition influences texture development in single-phase Fe alloys: Correlation between local chemical information, microstructure and recrystallisation [J]. Mater. Charact., 2022, 190: 112072 doi: 10.1016/j.matchar.2022.112072
14	Duggan B J, Tse Y Y. Crystal growth in deformed metals by an impingement and spheroidisation process [J]. Acta Mater., 2004, 52: 387 doi: 10.1016/j.actamat.2003.09.021
15	Bailey J E, Hirsch P B. The recrystallization process in some polycrystalline metals [J]. Proc. R. Soc., 1962, 267A: 11
16	Cram D G, Fang X Y, Zurob H S, et al. The effect of solute on discontinuous dynamic recrystallization [J]. Acta Mater., 2012, 60: 6390 doi: 10.1016/j.actamat.2012.08.021
17	Buken H, Kozeschnik E. Modeling static recrystallization in Al-Mg alloys [J]. Metall. Mater. Trans., 2021, 52A: 544
18	Cahn J W. The impurity-drag effect in grain boundary motion [J]. Acta Metall., 1962, 10: 789 doi: 10.1016/0001-6160(62)90092-5
19	Crumbach M, Goerdeler M, Gottstein G. Modelling of recrystallisation textures in aluminium alloys: I. Model set-up and integration [J]. Acta Mater., 2006, 54: 3275 doi: 10.1016/j.actamat.2006.03.017
20	Raabe D. A texture-component Avrami model for predicting recrystallization textures, kinetics and grain size [J]. Modell. Simul. Mater. Sci. Eng., 2007, 15: 39 doi: 10.1088/0965-0393/15/2/004
21	Raabe D. Multiscale recrystallization models for the prediction of crystallographic textures with respect to process simulation [J]. J. Strain Anal. Eng. Des., 2007, 42: 253 doi: 10.1243/03093247JSA219
22	Hutchinson B. Deformation microstructures and textures in steels [J]. Philos. Trans. R. Soc., 1999, 357: 1471
23	Zurob H S, Bréchet Y, Dunlop J. Quantitative criterion for recrystallization nucleation in single-phase alloys: Prediction of critical strains and incubation times [J]. Acta Mater., 2006, 54: 3983 doi: 10.1016/j.actamat.2006.04.028
24	Witcomb M J. Dislocation cell structure relation d = Kρ ^-1/2: The stacking fault energy dependence of K [J]. Phys. Status Solidi, 1974, 22A: 299
25	Huang X, Jensen D J, Hansen N. Effect of grain orientation on deformation structure and recrystallization behaviour of tensile strained copper [A]. 4th International Conference on Recrystallization and Related Phenomena [C]. Tsukuba: JIM, 1999: 161
26	Buken H, Kozeschnik E. A model for static recrystallization with simultaneous precipitation and solute drag [J]. Metall. Mater. Trans., 2017, 48A: 2812
27	Després A, Mithieux J D, Sinclair C W. Modelling the relationship between deformed microstructures and static recrystallization textures: Application to ferritic stainless steels [J]. Acta Mater., 2021, 219: 117226 doi: 10.1016/j.actamat.2021.117226
28	Montaño-Zuñiga I M, Sepulveda-Cervantes G, Lopez-Hirata V M, et al. Numerical simulation of recrystallization in BCC metals [J]. Comput. Mater. Sci., 2010, 49: 512 doi: 10.1016/j.commatsci.2010.05.042
29	Ratanaphan S, Olmsted D L, Bulatov V V, et al. Grain boundary energies in body-centered cubic metals [J]. Acta Mater., 2015, 88: 346 doi: 10.1016/j.actamat.2015.01.069
30	Yong Q L. The Second Phase in Steel Materials [M]. Beijing: Metallurgical Industry Press, 2006: 65
	雍岐龙. 钢铁材料中的第二相 [M]. 北京: 冶金工业出版社, 2006: 65
31	Lee H H, Jung J, Yoon J I, et al. Modelling the evolution of recrystallization texture for a non-grain oriented electrical steel [J]. Comput. Mater. Sci., 2018, 149: 57 doi: 10.1016/j.commatsci.2018.03.013
32	Mavrikakis N, Detlefs C, Cook P K, et al. A multi-scale study of the interaction of Sn solutes with dislocations during static recovery in α-Fe [J]. Acta Mater., 2019, 174: 92 doi: 10.1016/j.actamat.2019.05.021
33	Faulkner R G, Song S H, Flewitt P E J. Determination of impurity-point defect binding energies in alloys [J]. Mater. Sci. Technol., 1996, 12: 904 doi: 10.1179/mst.1996.12.11.904
34	Lejček P. Grain boundary segregation of antimony in α-iron: Prediction and experimental data [J]. J. Alloys Compd., 2004, 378: 85 doi: 10.1016/j.jallcom.2003.10.076
35	Pérez A R A, Torres D N, Dyment F. Sb diffusion in α-Fe [J]. Appl. Phys., 2005, 81: 787

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[2]	Yan ZHANG,Mingxing GUO,Hui XING,Fei WANG,Xiaofeng WANG,Jishan ZHANG,Linzhong ZHUANG. INFLUENCE OF DIFFERENT THERMOMECHANICAL PROCESSES ON THE MECHANICAL PROPERTIES AND MICROSTRUCTURE OF Al-Mg-Si-Cu ALLOY SHEETS[J]. 金属学报, 2015, 51(12): 1425-1434.
[3]	LI Zhengcao, CHEN Liang. IRRADIATION EMBRITTLEMENT MECHANISMS AND RELEVANT INFLUENCE FACTORS OF NUCLEAR REACTOR PRESSURE VESSEL STEELS[J]. 金属学报, 2014, 50(11): 1285-1293.
[4]	Xiang Zhao. EFFECTS OF ELECTRIC FIELD ANNEALING ON PLASTIC STRAIN RATIO (r VALUE) OF IF STEEL SHEET[J]. 金属学报, 2006, 42(8): 827-829 .
[5]	YANG Ping; O.ENGLER(Institute of Metal Science and Metal Physics; Aachen University of Technology; Kopernikusstr. 14; D-52056;Aachen; Germany) Now: School of Materials Science and Engineering; University of Science and Technology Beijing; Beijing;100083 Now: Los Alamos National Laboratory; Center for Materials Science; K765; Los Alamos; NM87545; USACorrespondent: YANG Ping; Tel: (010)62333436; Fax: (010)62332336. PARTICLE STIMULATED NUCLEATION AND THE FORMATION OF RSCRYSTALLIZATION TEXTURE IN Al-Mn ALLOY CONTAINING PARTICLES Ⅱ. Interaction Between Particles and Other Nucleation Sites and the Formation of Recrystallization Texture[J]. 金属学报, 1998, 34(8): 793-801.
[6]	YANG Ping; O.ENGLER(Institute of Metal Science and Metal Physics; Aachen University of Technology; Kopernikusstr. 14; D-52056;Aachen; Germany) Now: School of Materials Science and Engineering; University of Science and Technology Beijing; Beijing;100083 Now: Los Alamos National Laboratory; Center for Materials Science; K765; Los Alamos; NM87545; USACorrespondent: YANG Ping; Tel. (010)623s3Js6; Fax: (010)62332336. PARTICLE STIMULATED NUCLEATION AND THE FORMATION OF RECRYSTALLIZATION TEXTURE IN Al-Mn ALLOY CONTAINING PARTICLES Ⅰ. Deformation Zones Around Particles and Particle Stimulated Nucleation[J]. 金属学报, 1998, 34(8): 785-792.
[7]	SONG Renguo; ZHANG Baojin; ZENG Meiguang(Northeastern University; Shenyang 110006)(State Key Laboratory of Solidification Processing; Northwestern PolytechnicalUniversity; Xi'an 710072). THE STRESS CORROSION AND ROLE OF Mg SEGREGATED TO GRAIN BOUNDARY IN 7175 ALUMINIUM ALLOY[J]. 金属学报, 1997, 33(6): 595-601.
[8]	WANG Wendong; ZHANG Sanhong; HE Xinlai(University of Science and Technology Beijing; 100083)(Manuscript received 93-09-21. in revised form 94-01-26). DIFFUSION OF BORON IN Fe-BASE AND Ni-BASE ALLOYS[J]. 金属学报, 1995, 31(2): 56-63.
[9]	ZHAO Xiang(Northeastern University; Shenyang 110006); SEKI Fumie; ITO Kunio(Universily of Tokyo; Japon); YOSHINADA Naoki(Nippon Steel Compony; Japan) (Manuscript received 1994-03-07; in revised form 1995-01-12). INFLUENCE OF DISSOLVED CARBON CONTENT ON RECRYSTALLIZATION γ TEXTURE IN ULTRA-LOW CARBON DEEP DRAWING STEEL WITH HIGH PURITY[J]. 金属学报, 1995, 31(18): 262-265.
[10]	D U Guowei;WANG Zheng;ZHANG Dezhi;XIAO Jimei(University of Science and Technology Beijing)(Manuscript received 27 January;1994). HIGH TEMPERATURE INTERGRANULAR EMBRITTLEMENT OF Ni_3Al-Cr-Zr-B-Mg ALLOY[J]. 金属学报, 1994, 30(9): 394-398.
[11]	WANG Yanbin; WANG Anrong; CHU Wuyang; XIAO Jimei (University of Science and Technology Beijing). X-RAY TOPOGRAPHIC STUDY OF HYDROGEN DAMAGE IN Fe-3 wt-%Si ALLOY[J]. 金属学报, 1992, 28(9): 52-56.
[12]	LU Feng;CAO Fengyu;LI Chengji;ZHANG Yongxiang;CHEn Yonggang University of Science and Technology Beijing Beijing Institute of Machine Tools Correspondent Faculty of Metallograph; University of Science of and technology Beijing; Beijing 100083. ALLOYING BEHAVIOUR OF Ca IN 58CrV STEEL[J]. 金属学报, 1992, 28(6): 7-12.
[13]	ZHANG Dongbin;WU Chengjian;YANG Rang University of Sciencs and Technology Beijing. GRAIN BOUNDARY SEGREGATION OF P IN Fe-P AND Fe-P-Ce ALLOYS AND EFFECT ON THEIR BRITTLENESS[J]. 金属学报, 1991, 27(2): 33-36.
[14]	LIU Yansheng;ZHAO Xiong;LIANG Zhide Northeast University of Technology; Shenyang Department of Materials Science and Engineering;Northeast University of Technology;Shenyang 110006. COLD ROLLING TEXTURE AND RECRYSTALLIZATION TEXTURE OF CROSS SHEAR ROLLED COMMERCIAL COPPER[J]. 金属学报, 1990, 26(3): 126-130.
[15]	LI Guangfu;WU Rengeng Harbin Institute of Technology Ll Guangfu; Division of Metallography; Harbin Institute of Technology; Harbin 150006. IMPROVEMENT ON SUSCEPTIBILITY OF ULTRA-HIGH STRENGTH STEEL TO STRESS CORROSION CRACKING BY HIGH TEMPERATURE QUENCHING[J]. 金属学报, 1989, 25(6): 70-73.

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