Recrystallization and Related Phenomena. Texture Evolution of IF Steel Due to Recrystallization.

Hashimoto, N.; Yoshinaga, Naoki; Senuma, Takehide

doi:10.2355/isijinternational.38.617

Cited by 44 publications

(23 citation statements)

References 7 publications

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“…For IF steel sheets, EBSD studies have shown that nucleation occurs within the dense structure of the deformed γ-fiber grain orientation and that the resulting nuclei grow into deformed α-fiber components in steel sheets. [46][47][48] From previous theories and observations, it is likely that when γ-fiber with high value of the Taylor factor is present in the cold-rolled sheets similar to those of Type A, γ-fiber develops mainly after recrystallization. In other words, the development of γ-fiber texture in cold-rolled sheets is important in producing sheets that have strong and sharp γ-fiber and a very high r-value.…”

Section: Effect Of Cold Rolling Texture On Recrystallizationmentioning

confidence: 99%

Effect of Texture on r-value of Ferritic Stainless Steel Sheets

2011

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The effects of cold rolling texture on the formation of recrystallization texture and the relationship between recrystallization texture and r-value were investigated for sheets of titanium-stabilized extra-high purity Type 436L and Type 409L ferritic stainless steels. The recrystallization texture and average r-value were affected by the cold rolling texture. Annealed sheets with a sharp γ-fiber texture and very high average r-values were obtained from cold-rolled sheets with a strong γ-fiber texture (Type A). On the other hand, the {h,1,1}<1/h,1,2> fiber texture developed from cold-rolled sheets with a strong α-fiber texture (Type C). In terms of the relationship between {111} intensity and the average r-value, chromium content had less effect than the cold rolling texture. The planar anisotropies of r-values and the average r-values of Type 436L and 409L sheets with Type A cold rolling textures agreed well with those calculated from the textures in the center layers by using the relaxed-constraints model and the CRSS ratio τc{211}/τc{110} of 1.1. On the other hand, for the sheets with Type C cold rolling textures and a marked texture gradient, it was necessary to consider the texture gradient in the thickness direction. The texture inhomogeneity by the orientations other than {111} texture affected the relationship between {111} intensity and average rvalue.

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Section: Effect Of Cold Rolling Texture On Recrystallizationmentioning

confidence: 99%

Effect of Texture on r-value of Ferritic Stainless Steel Sheets

2011

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“…It has been widely accepted that TiS is predominantly formed at temperatures higher than Ti 4 C 2 S 2 . [51][52][53][54][55][56][57][58][59][60][61][62][63][64][65][66][68][69][70][71][72][73][74] In addition, (d) solubility products of TiS and Ti 4 C 2 S 2 in austenite region have been proposed by many groups. 31,35,37,44,52,53,62,68) It has often been stated that sulfide precipitation in austenite phase can be fully described through thermodynamical calculation, but all the calculations are not always consistent with each other.…”

Section: Purpose Of Our Studies and Reviews Of Past Reportsmentioning

confidence: 99%

Sulfide Precipitation in Titanium-Added Steel with Residual Level of Copper (1) —Precipitation in Austenite Region—

Ishiguro¹,

Murayama²,

Fujita³

et al. 2009

Mater. Trans.

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The authors previously reported that even a trace level of copper (0.01% Cu) acts as a sulfide-former to form copper sulfide (Cu-S) in nonTi-added steel in which Mn has been thought to be the only sulfide-former so far. A new concept of copper-related sulfide precipitation is now extended to Ti-added steel. In addition, the total sulfide precipitation in Ti-added steel is reconfigured with the new knowledge of Cu-S. The new concept is shown in three consecutive papers. This first paper focuses on the sulfide precipitation in austenite-heat-treated Ti-added steel.Through TEM observation and quantitative chemical analysis, it is reported that the sulfide precipitation in austenite-heat-treated Ti-added steel reflects not only the precipitation in the austenite region but also the inevitable precipitation behavior during the cooling process from austenite to ferrite region, especially trace-level-Cu-induced Cu-S precipitation in ferrite region during rapid cooling. The mechanism of the inevitable sulfide precipitation during the cooling process is mainly based upon TiS-decomposition-induced morphological change and the reprecipitation of sulfur which remains solute over precipitatable limit during the heat-treatment in austenite region, and is precisely discussed in relation with Cu-S precipitation. Purpose of Our Studies and Reviews of Past ReportsThrough three consecutive papers, 1,2) the authors demonstrate the comprehensive concepts of sulfide precipitation in Ti-added steel in austenite and ferrite regions with the addition of a new concept of copper sulfide (Cu-S) precipitation induced by a small amount of 0.01%Cu, as well as the rarely-mentioned concept that Ti 4 C 2 S 2 and MnS are formed in ferrite region. The first paper focuses on sulfide precipitation in austenite region, including the phenomena in austenite-heat-treated Ti-added steel with the subsequent various cooling pattern.The following review provides explanations and comments on past studies of Cu-related precipitation, together with our purposes. These items are mentioned only in this paper, the first part of three consecutive papers. Therefore, the following description includes phenomena in both austenite and ferrite regions, because these phenomena are related to each other and cannot be completely separated. Table 1 shows the overviews of past studies on both Curelated precipitation in steel and sulfide precipitation in steel, together with the purpose of the three consecutive studies. Each item below is referred to as a ''parenthetic No.'' in Table 1. First of all, it has been believed as an established theory that (1) a small amount of Cu in non-Ti-added steel exists as solid solution, and many people have not paid any attentions to it. However, as our group has already pointed out, (2) such a trace level of Cu acts as a sulfide-former to form copper sulfide (Cu-S) in non-Ti-added steel whose sulfide-former is only Mn (more precisely, 0.01%Cu). [3][4][5][6][7][8][9][10][11][12][13][14][15][16][17][18][19][20] The first purpose is (#1) to...

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“…Both the deformation microstructure (particularly the in-grain shear bands) and the deformation texture influence the orientations of the recrystallized grains. [5][6][7][8][9] During the annealing of as-rolled interstitial-free (IF) steels, the presence of shear bands gives rise to recrystallization nuclei with ͗111͘//normal direction (ND) type orientations. These components are further intensified when the rolling direction (RD) fibre components are absorbed during the later stages of recrystallization.…”

Section: Introductionmentioning

confidence: 99%

The Deformation Microstructure and Recrystallization Behavior of Warm Rolled Steels.

Humphreys

Toroghinezhad

et al. 2002

ISIJ International

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The deformation microstructure of various warm (ferritic) rolled steels was characterized and its influence upon the subsequent annealing behavior determined. The materials investigated included three interstitialfree (IF) steels (stabilized with either titanium or niobium), an extra low carbon (ELC) steel, and four experimental low carbon chromium steels with varying levels of boron, nitrogen and phosphorus. Single pass rolling experiments were conducted in a pilot mill at temperatures between 440 and 850°C and the asrolled microstructures were examined using optical microscopy. Particular attention was paid to the nature and intensity of the in-grain shear bands produced. Partial annealing was conducted to examine the nucleation of recrystallization in the deformed microstructure. Shear bands of moderate intensity were usually formed in the IF steels, which tended to be insensitive to rolling temperature. For the ELC steel, intense shear bands were formed at low rolling temperatures, but at higher temperatures this intensity was found to be drastically reduced. The development of shear bands at the higher rolling temperatures was significantly enhanced by alloying with chromium. The differences in shear band frequency and intensity are explained in terms of the dynamic strain aging behaviors of the various materials. Recrystallized grains were found to nucleate preferentially on the shear bands during annealing, regardless of their morphology or intensity.

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Recrystallization and Related Phenomena. Texture Evolution of IF Steel Due to Recrystallization.

Cited by 44 publications

References 7 publications

Effect of Texture on r-value of Ferritic Stainless Steel Sheets

Effect of Texture on r-value of Ferritic Stainless Steel Sheets

Sulfide Precipitation in Titanium-Added Steel with Residual Level of Copper (1) —Precipitation in Austenite Region—

The Deformation Microstructure and Recrystallization Behavior of Warm Rolled Steels.

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Recrystallization and Related Phenomena. Texture Evolution of IF Steel Due to Recrystallization.

Cited by 44 publications

References 7 publications

Effect of Texture on r-value of Ferritic Stainless Steel Sheets

Effect of Texture on r-value of Ferritic Stainless Steel Sheets

Sulfide Precipitation in Titanium-Added Steel with Residual Level of Copper (1) &mdash;Precipitation in Austenite Region&mdash;

The Deformation Microstructure and Recrystallization Behavior of Warm Rolled Steels.

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Sulfide Precipitation in Titanium-Added Steel with Residual Level of Copper (1) —Precipitation in Austenite Region—