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Title Modes of Grain Growth in Cold Rolled 3.25% Al-Fe Alloys With and Without Dopant S

Author(s) Nakae, Hitoshi; Goshi, Noriaki

Citation Memoirs of the Faculty of Engineering, Hokkaido University, 13(4), 297-308

Issue Date 1974-03

Doc URL http://hdl.handle.net/2115/37896

Type bulletin (article)

File Information 13(4)_297-308.pdf

Hokkaido University Collection of Scholarly and Academic Papers : HUSCAP

ft

Modes of Grain Growth in Cold Rolled 3.Z5% Al-Fe

Alloys With and Without Dopant S

Hitoshi NAKAE* ･ Noriaki GosHI**

(Received July 27, 1973)

t. Abstract

In the modes of'grain growth in cold rolled 3.25% Al-Fe alloy sheet, some

points still remained to be explained. In the first point, the growth curves ob-

tained experimentally are rather complicated in contrast to the simple exponential

curve anticipated from a driving force based on the grain boundary energiesconstituted by an aggregate of small grains formed in primary recrystallization.

In the second point, the texture with (100) [OOI] orientation qs the main component

is formed in Al-Fe, whereas (110) [OOI] is seen in Si-Fe' during the growthstage from nearly the same textures in as-rolled and primariiy recrystallized states

of both alloys.

The authors assumed a local deviation in compositions from nominal ones

along the grain boundaries possibly motivated by boundary migration, and have

associated them with a characteristic point of phase diagrams of the alloy systems

at which a local phase transition (e.g. from solid to liquid) in a region of deviated

composition along grain boundaries could occur.

Based on the above the behavior of growth may be described by a charac-teristic rate and habit of growth in tne presence of a liquid phase and thereupon

a complicated course in growth curves in the alloys and a preferential growth of

(100) [OOI] component in Al-Fe alloy sheet could reasonably be explained.

I. Introduction

The recrystallization texture of 3.25% Al-Fe alloy sheet is known to consist

of a main component of (100) [OOI] in contrast to that of (110) [OOI] orientation

iin 3.25% Si-Fe alloy sheet, while they show simiiar physical properties with

regard to electrical resistivity, magnetic permeability, and mechanical tensile be-

haviorsi),2).

In the recrystallization of Si-Fe alloy sheets, the main component of the

texture has been known to be strengthened by a small addition of sulfur, titanium,

niobium etc3)N7). The effects of sulfur, and manganese have been reported by

May, Turnbull and one of the present authors8)NiO).

* Department of Precision Engineering, Faculty of Engineering, Hokkaido University, Sapporo,

Japan. ** Division of Precision Engineering, Graduate School of Engineering; now assigned to Hitachi

Kinzoku Co., Kawagoe, Tolcyo, Japan.

298 Hitoshi NAKAE and Noriaki GosHI

It is a!sp'.kriown, that the texture in Si-Fe alloy under certain conditions has

(100) [OOI] component as the main component, e. g. in grain growth in thin sheet

or often at an annealing temperature exceeding 12000Cii)'"i3).

It would be worthwhile to discuss the effect of sulfur on the grain growth

behavior in Al-Fe alloy with the special reference to the results obtained in Si-Fe

alloy containing sulfur and to elucidate the mechanism involved which leads to

cause the difference in growth behaviors in Al-Fe and Si-Fe alloys.

II. Experimental proeedure

The specimens were melted in a vacuum furnace by adding different amounts

p.f sulfur to 3.17% Al-Fe base alloy. After hot working, they were cold rolledu'ntil the final thickness 6f O.35 mm. The reduction estimates 75%. The chemical

compositions are listed in Table 1. in which the content of sulfur was O.O04,

O.060, and O.148% in No. 1, 2, and 3, respectively. No sulfur was doped in the

No.1 specimen and the high content of carbon in No.3 specimen was due tothe carbon contained in the doped sulfur material which might give no essential

effect on the results.

The specimens were annealed and observed at 500C from 600 to 7000C andat 1000C intervals from 700 to 12000C with an isochronal aRnealing time of 1 hour.

Optical niicroscope, Gonio-microscope'`), X-ray and torque magnetometer were em-

ployed for the observation of structures and the determination of textures,

TABLE 1 Chemical composition of the Al-Fe alloy specimens (wt %)

/ .

No. 1

No. 2

No. 3

Al

3.17

3.17

3.17

c

O.O07

O.O09

O,030

si

O.Ol

OOI

O.04

s

O.OO4

O.060

O.148

P

O,O02

O,O02

O.O02

Bal.

Fe

Fe

Fe

III. Experimental results

The textures were determined by X-ray method in the three specimens with

various sulfur contents in cold rolling, primary recrystal!ization and the grain

growth, a qualitative analysis of the shift rate of the textures during grain growth

was made by observations of magnetic torque curves together with the X-raypole figures.

1) Textures as rolled

.The pole figures are shown in Fig. 1(A), (B) and (C) in which the texturesafe constituted by the three major components of (112) [IIO], (111) [112] and

(100) [Olll. The (110) [OOI] and (100) [OOI] components which wiil become the

major components of recrystallization texture thereafter were observed by the

orientation etch-pit method using a Gonio-microscope, and it was found that their

concentrations became sharper with the increased sulfur doping.

t./

Modes of Grain Growth in Cold Rolled 3.25% Al-Fe Alloy 299

(a) spec±men : Nb.1RD

J2 l6

t'">

1 1""o'

is ltt -x JS txX.P-2--[6g4e,ti

8

I6 O([ilil ji

r-hkN,

ILs.

42

x."r--`-"'-JXttt- 1----m----!-

2N ,, "

2TD

(a) Specimen.: No.1

IRD 4 /2

,"

sUff `4.Sti

(b> Spectmen : No.2

RD

N / !f

./ o o

o ""

ts J{ lt st,tt Xi,,1 3216842i'ltt J-- -"--- "Jf

-----H-- --- l--t-------"--

42 '.

15X 16

V2

t t t L i , 1 N O ltsst Xo .-. -s I6.: oj-)2[)

rNrD

2

(b) Speo±men : No.2

RD 4 4 Ht>:S---.-L{.).`-.-F.J..-.LL.-ltl'--XN".. -

j-tt-(:;;1 ttr---stlxtS--J ,,."-il...-r.=t :,)oi>X'li;x.../.ir:..:.

11 iLt.'t-jt.---tJt') lt-ts-ks--YJokLtS

it-t l ."--f/'･:2 52 'x i-'-:;j fi"r Jlll..--J".t)iitttt-F-----Lt'xix Xii 'k.:li--ii-x..j.-.

sstl'"'l','-.-'s -l<;" >t?'- ･'i /)iiJS)lli,l'

(o) Speaimen

--L-Y

sl

'.,l

'

o

t No.3RD

0 tftt ix [x ,i .:, < s: t, s21842/ v. ----･ .IS

o

c,tr[J- :E,-Ltl--:h,.

..32

<i)ii

s[6･O

6

i1t'

42

rrD

Fig. 1. (110)-pole figures of cold rolled 3,17%

Al-Fe alloy sheets by 70% to 3,5mm in thickness. Symbols A, 0 and [] indicate (111) [II2], (112) [112] and (100)

[Oll] poles respectively,

2) Primary recrystallization textures

Thetexturesofthesethree 'annealed at 7000C for 1 hour which

primary recrystallization. The

same components as cold rolled texture

[OOI], and a fair!y large part of

spread though the (li2)[IIO], (111)[112]

ened by the addition of sulfur. By

of (110) [OOI] and (100) [OOI] components

(o) Specimen : No,3

RD i6e i 4

2.../ 'X..A 1i ',/ tl,(.l. 1¥'ilKI,,.geq tt,,l,' il, "NL -2

'Z/- -' iu--:--ig, ;'`t- .]-,,i'', ):li,c{i-9-ies,

Fig. 2. (110)-pole figures of cold rolled 3.17%

Al-Fe alloy sheets annealed at 7000C for 1hr in hyarogen atomosphere.

D

specimens are shown in Fig. 2(A), (B), and (C),

seems to be at a step generally expressed as

components constituting the texture are of the of (112) [IIO], (111) [112], (110) [OOI], (100)

random components, with a rather increased and (110) [OOI] components are strength-

optical microscopic observation, a major part

are of recrystallized grains, while other

300 ' HitoshiNAKAEandNoriakiGosHI

components are still in the recovery stage.

In any event the cold rolled and primarily recrystallized textures of 3.25%

Al-Fe alloy may be considered to be essentially simiiar to those observed in co!d

rolled 3.25% Si-Fe alloy with the same effect of sulfur.

In a 3.25% Si-Fe alloy sheet, each component of the same orientation ap-

peares as a group forming a colony or flora in each orientation and among them

the (110) IOOII and (100) [OOI] components existed near the surface of the sheet

with small orientation spread, whereas the (111) [112] and (112) [1101 components

existed in the inner part of the specimen with a rather large orientation spread.

(a) Spee±men : No.1 RD (.1irLE.)."l"-:'--ttA-.1:es (a)specimen:No.1 Ro

.(ci}i:',,fJ,,(li3`il..":ei' eq@). .@./kJ':' ,{,,O o

.,,,,ri,:Ill,1･3Lll,Il,, t;)o,,, /ftzztii?s!a.i.1;.' .-,c･,-.,'L' lt--NgS.II-.),

-s Nk

(b)

(c)

,ci:l,1, ,&･ /.'V'"ia',--i st.-kg7.vi.EA..ilSgks)N

ss

t

Spec±men : No.2

RD x-. g)L. ,...-7 ------@-t--)ICIstS･

'L.@"->

il･:' n, c] x .' "' o'l@' Cit,`i,".(s,IOII':fdls'.ii{lii.Sl'e"-,t'i6'e".i(-'.J.i..,J,.,,

Specimen : No.3

RD l1 ljx ". /1./(･6"of '2';' f',;1'1.,`'?tf,'ll:I.{S'l`-l".iis.-),/

s.f}.V'ito/ Ii .J..lc@-l ([:;,/'i.IJ.i@･/ ,1.:-.J.;,,,,.:,

trX - ti'u･2;Se",{p{'6･--1/;t;:,Itt'"'"fi"t9Sr-'

i ---L-----n-"----+r"" Ng!Fig. 3.

for 1hr in

)

arxe-･t" .

Iti'l lti;ttt,.,]･

i,i (., ,v 1'l 1..fLtT)li'ILxU

I)lk.0t Xx 4---L V t -sN (.'r c, SXxbl

o

C:･i>s

tlS:.)ir' T

@-

'lttt -

Iotk.1

1'

ss-s.

lt :,

:;., ,Z

t,G}

(l)l....@'

ltlt )lit<-Jtrit

T

(100)-pole figures of cold rolled 3.17%

Al-Fe alloy sheets annealed at 1200eC

hydrogen atomosphere,

b)

'-,/rtll9i'

--'Nv{E)iL,, i:'9)i

.ltiti Ll

--- o'kdl

Spsctmen

@

t' @JW/'

O /s"-Sir

@fl

,,11 +: No.2

RO Cfftt ----i

..;] (gSS))

" s) aj @'ts-'64

/-- ･'s 1 EiiO･7

(bl + t

N@"'K'/"ep,h'

S ,.g.･,ee

"l

c=.'J'{st- )}

,o

ditlll' [($$'

tr--- rt .JJ-@

'rD

' l i- NsxN ll @>. s"'t. 'sxS .ig rwr'IN

Xv s.: "" @..l(Ili-") )i `"N g (j'IslT

(c) Spec±men : No.3 RD .ec@.$&"c@-s;i"/el' .I( .`, Q,･

"ot,`'tadi + itcsti,"gy,g.sl,1,.,"T

Fig. 4. (110)-pole figures of cold rolled 3.17%

Al-Fe alloy sheets annealed at 12000C

for 1 hr in hydrogen atomosphere.

l

Modes of Grain Growth in Cold Rolled 3.2595 Al-Fe Alloy 301,

Then the formers are known to grow dominantly against the latters at the stage

of grain growthiO). These behaviors may also be expected to occur in Al-Fe alloy

sheet.

3) Textures during and after grain growth

(i) Ii'ble figure

The poie figures of (100)- and (110)- poles on on the specimens, annealed at

12000C for 1hour are shown in Fig, 3(A), (B) and (C), and Fig. 4(A), (B) and (C)

respectively. In the figures, the growth seems to be carried both in (110) [OOI]

and (100) [OOI] components by the consumption of other residual components, in

contrast to the 3.25% Si-Fe alloy sheet whose growth compgnent is mainly a(iiO)IkOOtih]e O"ioe.n:a/ipOenc'imen, the texture is composed of two main components of

(110) [OOI] and (100) [OOI] with a weak (112) [IIO], (111) [112] and a dispersed

(100) [Oll]. In the No. 2 specimen, the main components are the same as in

No. 1, but other components are hardly seen. In the No. 3 specimen, the maincomponents are also the same as in the above two specimens, however (111) [11-2]

and (100) [Oll] components are seen at a very small degree. In these threespecimens in common, the (110) [OOI] and (100) [OOI] components which form the

main part of texture are seen with'a siight dispersion of orientation around the

common [OOI] axis.

(ii) Magnetic tof'que curve ･ The magnetic torque curves were taken on the specimens annealed at the

temperatures from 6500C up to 12000C and a -tendency of texture shift during

grain growth was observed qualitatively. Although a magnetic torque curve of

a polycrystalline specimen is the statistical mean of basic curves for the orienta-

tions of all the crystals, the effects of several' preferred orientations will be con-

sideredbriefiyreferringtoFig.5'3). r . ,,t For (100) [OOI] crystal, the magnetic torque L is given by

L--(Kl!2)sin4cr, ' ･ for (100) [Olll crystal which is one of the components of the deformatioh tex-

ture and an orientation obtained by a rotation of 450 from the above crystal, . ･

' L=(K12)sin4cr, ' ' 'and for (110) [OOI] crystal,

.tl L--(Kl14)sin2a-(3Kl/8)sin4a, ., .. 'where Kl is the first anisotropic constant, a the direction cosine of [OOI] directien

referred to the X axis of the three dimensional coordinate. In this case, other

direction cosines of P and r referred to Y and Z axes disappear. The secondanisotropic constant K was neglected because of its meager contribution to the

torque value. The torque values of other components such 'as ･(111) [112] and

302 Hitoshi NAKAE and Noriaki GosHt

(71 )

(a) 'r"ojcuao (/av(zv/)(b) (c) CfOO?(ottJ

CB? tx foo M g. $ oo m` ua

× an v wO ..sl!

g -mo

q, -40

ts S!"-60

R --to

-mo Fig.

AIX1 xx

1

/

7tlxsu /

t-

/,te-'

N

rae

x

x //ANx

7-"x,

･su

Ze

iVb./ sleci`menrZev7nenleta;2

htb, 2

,Vb, 3

3po

NK･yf' Xx

Nx -/i

6oO 90

/

Xxv/

curvesrolled

N'>,･cl`' lx

xx

Ny

a few typical

@･2:-.g,zge-d

1 bn11

/ ,vlo-/sv'ec2 ,e"jo,/.d)

BMle 'fft?m

irv Diteet'lr

5.Torque of. singlecrystals(A)and ofcold 3.17%Al-Fealloysheetsofasrolledand annealed at 7000C for 1 hr in hydrogen atomosphere (B).

'(112) [IIO] orientations will also be negiected in the analysis for the same reason.

As for the (110) [OOI] and (100) [OOI] orientations the torque curves are in

phase, therefore, maximum torque values are associated to the' degree of alignment

of the (110) [OOI] plgs (100) [OOI] colnponents. The (100) [Oll] compQnent is anti-

phase to the former two components, hence its existence in the texture diminishes

the maximum torque values markedly. As for the quantitative balance of the

(110) [OOII and (100) [OOI] components in the texture, the ratio bf the maximum

values of the first to the second may be estimated, since they are O.43 and unity

with (110) [OOI] and (100) [OOI] orientations respectively. The magnetic torque

curves taken for the specimens over the entire range of recrystallization show

the characteristic curve shape of (110) [OOI] plus (100) [OOI] components and there-

on the analysis wi11 be made. In the primary recrystallization, the maximumtorque values show a decrease･with the increased sulfur doping, while the torque

ratios are Iarge and almost the same in No. 1 and 2 and small in No. 3 as seen

in Fig. 6(A)･and (B). They will be explained together with the pole figures in

'-'x vNsg

gMbx

,IE.

-",

)l}l

g

g.g

s

G-

%3:t

2DO

1co

f20

80

ua

0

Modes of Grain Growth in Cold Rolled 3.25% Al-Fe Alloy 303

(a)

o-----o

pt-oa･-o

No,/No, 2

No･ 3

spectmenspecLmenspecbmen

o/o- ---

o---6-

7i----n" l

---Ck

./-9enen

1-' o

/!zlZl

/-n

l

..d/t"t

･----- o-

1･0

(b)

08'

" s >･'-< .rr:=.=-'

o-' s ' --s -t--.-o･6 o

.

-- -.--- -.--.-4f -

o4

o

06oo 7oo 800 9oo10CV tpo (2VO

7remperatOre(oc) .

Fig, 6. Maximum torque values (a) and peak value ratios (b) of cold rolled 3.17% Al-Fe alloy sheets annealed at various temperatures for 1 hr in hydrogen atomosphere.

'Fig. 3 as having (110) [OOI], (100) [OOII and (111) [112] and (100) [Oll] components

which exist commonly in these three specimens and the former two components

occupy a large part of the specimens in which the (110) [OOI] is the mostdominant.

As for the tendencies of quantitative balance of (110) [OOI] and (100) [OOI]

components in the textures during the growth, a torque ratio versus temperature

curves in Fig. 6(B) may be considered. A increase of the torque ratio against

temperature would mean that the growth of the (100)[OOI] component was

304 Hitoshi NAKAE and Noriaki Gos}i[I

dominant over the (110) [OOI] component during growth. The tendency wasmost marked in the No.3 specimen. Here the growth of these major compo-nents may be achieved by absorbing the other components such as (111) ll12],

(II2) [IIO], (100) [Oll] and others existing in the primary recrystallization texture.

These tendencies may be characteristic only in Al-Fe alloy and somewhat different

from those in Si-Fe alloy whose dominant growth component has a (110) [OOI]orientationiO).

The maximum torque values at raising temperatures show at first a directincrease in the No. 1 specimen presenting no sulfur practica!ly, while remaining

unvaried uptill 8000C and 10000C in the No. 2 of moderate suifur and the No. 3

of the highest sulfur respectively. Then, a retardation of growth beginning at

9000C is observed in No. 1, whereas no retardation is seen in No. 2 containing

sulfur. (also in No. 3 specimen)

The (111) [112] and (112) [110] components consisting a main part of as rol!ed

texture remain slightly in No. 1 and considerably higher in No. 3, while they

are hardly seen in No. 2 speeimen annealed at 12000C for 1hour.

IV. Discussion

The grain growth invoMng a grain boundary migration in alloys is cornpared

to the crystallization or crystal growth of many other substances (e.g. ionic or

homo-polar) in which crystals grow from a vapor or Iiquid as well as from asolid phase'6). In these substances, a growing crystal generally tends to be free

of defects and foreign atoms, and crystalllzation is known to be one of the ways

Direction of Moving Boundary

- -- t -- -i -- 1-t i -- -t -- . ' ii- -- -- -- - t-t-- d -- li-l --- --- - , I- --+ --it - . ,.' Nominal Cornposition

- t-- , -.-- i--- 1- , -- d-- -- -- -- - t -- --- i 4i ' , -- - -, ti - -- i- -- i- tt-t t--l- - /

Region Freed o£ Foyeign Atonis (i.e. Pure Fe)

Fig. 7. Regions of deviated

and forward of movingcomposltlons boundary

-- t--t- --v--l- -- t -- -- - --t-- -J ---t -)i -- t-- -i -i- i --- - -4- - -t -- --t- - --l - i----- - ---- - i. - -t---- - ----- 1 il }--- d- t- -t - -t-- - i-- --i- i v-- -- 4-i-----:-ti- - - -- t- -i- -t -t--t -t - -- - -- - t- -----t-J- -- - -i--i-li ; i---- -t -i-1 -- - -i - i-- t- i -i--- - - s- -t--- - -i f- - -ll- i- --t- ii -i ---1 - - --Ft- - - -) -i -- -i-t - --t - lt Jd--- - -t --- t --i j -q - -ttii - -i -} - --F -i - --i--J - ti - i- -l-- t- - r--t- - ---- ---- N Region Enviched with

Foreign Atoms lrom nominal one afterward

(Sehematic)

Modes of Grain Growth in Cold Rolled 3.25% AI-Fe AIIoy 305

of purifying materials. The tendency may be due to the familiarity of interac-

tions between respective like atoms and foreign atoms which are transported to

meet by grain boundary migration. It may not be unreasonable to extend the

thinking also to a grain growth in alloys. Then, the hinter and forward regions

of a moving boundary could tend to be of free and rich regions of foreign atoms

respectively (cf. Fig. 7).

In the case of Ai-Fe and Al-S-Fe alloy systems, a foreign atom may imply

the alloying addition Al as well as the doped element sulfur. In the course of

achievement of grain growth, the inner part of the moving boundary wili become

rather pure Fe, while the outer region may be enriched by Al and S.

This phenomenon may be a tendency against a thermodynamical or phaseequilibrium. Then, for the sake of high atomic diffusivity in meta!s, the regions

with deviated cornpositions from nominal one will become a transient and minute

layer inside and outside the moving boundaries. If either one of these regions

meet the characteristic points or transition lines corresponding to its deviated

composition on the phase diagrams of the al!oys at raising temperatures, they will

be subjected to a phase transformation in the alloys in which no transformation

appears until an intersect!on with a solidus line over 15000C in nominal composi-

tions. Then, the alloy can meet the A3 point, eutectic points and solidus Iine in

their deviated compositions at the stage of grain growth. If a iiquid phase ap-

pears in a grain boundary, the grain growth will be obeyed by a general feature

of crysta! growth in the presence of a liquid phasei')Ni9) for which much work on

the characteristic rate and habit of growth has been reported.

For the discrimination of the process, the phase diagrams of ternary Al-S-Fe

alloy system should be referred to. But we have, however, no sufficient information

concerning this, it is referred to the diagrams of each binary alloy system of

Al-Fe and S-Fe, assuming that the characterstic points of these binary alloy

diagrams will be linked with the characteristic points of the ternary systems to

some extent and also give some significant knowledges on the effects').

Now, the growth curves expressed by a torque maximum and a torque ratiowill be referred to the phase diagrams of the binary alloy systems20) (cf. Fig. 8).

The retardation of growth observed on the torque maximum begins at 9000C in

plain Al-Fe alloy which has also been observed in Si-Fe alloy coincides with A3

transformation in pure Fe at 9100C. It may be deduced that at the inner region

of moving boundaries, the alloy may tend to be rather pure iron and may give

rise to A3 transformation or stagnation of boundary migration. The fact that

no retardation is observed in Al-Fe alloy doped sulfur wi!1 support the above

explanation, since only a smal! addition of S to Fe degenerates the A3 transforma-

tion drastically as seen in the phase diagram of S-Fe system.

The increased rate of growth and the growth of (100) [OOI] component ob-

served at 10000C in Al-Fe alloy doped sulfur which is also observed as a growth

of single (110) [OOI] component in Si-Fe alloyi5) may be associated to the eutectic

point of 9880C in Fe-FeS system. The coincidence of another eutectic point at

306

feo

1600

1400

1200

1000

BOO

600

20

Hitoshi

at. o/.

40 60

NAKAE

Uo¢L]-HULoQEs

80

and

At 1OO

Noriaki GosHI

fo

O 20 40

t

t

i

1

1

I

at.Oh

N N x

91oo

kN

x

N

x

N

x x x xxx

N

r

60 80

si

1001

fe - At

s

1

1

1l

t

t

l

91oe

NN

foo

1600

14oo

12oo

10oo

li ll12ooe li1212a

F:e - Si

at.ofa

20 40 60

12osO

s'

Fe-S

ll xX t IN - ls 9sBe

Fig. 8. Phase diagrams of alloy system of Fe-Al, Fe-Si and Fe-S20),

11600C to the growth would appear, if the plots against temperature were taken

precisely around the point, though it was not obvious on the curves.

A mode of crystal growth in the presence of a liquid phase may be compared

to the dendritic growth in a cast ingot of iron whose direction and plane of

growth relative to a crystal coincide with <100> direction and {100}. plane respec-

tively.

In the grain growth in alloys, the process may, however, be carried in a

two-fold manner, firstly to minimize an interfacial energy which depends chiefiy

on the geometry of interfaces and then to satisfy the preference for growth in

crystallographic planes between the grains facing each other.

As for the growth of (100) [OOI] component in Al-Fe a!ioy in the' growth

stage, it may be ascribed to the lower solidus line against temperature in the Al

rich side of the phase diagram to the extremity of 6600C of melting point of Al.

The effect will, however, be integrated and become conspicuous although occurring

in a minute region, because the reacting regions travel through the matrix fol-

lowing the migrating boundaries.

Another remark will be made here to the effect that the temperature at which

the growth of (100) [OOI] component begins in Si-Fe alloy also corresponds to the

eutectic points 1200, 1208 and 12120C of the alloy.

V. Conclusion

The conclusions brought about from the experimental results on the texture

formation in cold rolled 3.17% Al-Fe alloy with or without doped sulfur will be

Modes of Grain Growth in Cold Rolled 3.25% Al-Fe Alloy 307

' 'summarised as follows. - (1) The as-rolled and primarily recrystallized textures were essentially the

same at each stage as those observed in 3.25% Si-Fe alloy regardless of sulfur

content, being

(i) the as-rolled textures were composed of (112) [IIO], (111) [112], (100)

[OOI] and other random components in the descending order of con-

centration and (ii) the primarily recrystallized textures were composed of nearly the same

components of as-rolied textures with a rather increased spread, ap-

pearing a (llO) [OOI] component as minute but distinctly recrystallized

one. (2) During the grain growth, the (110) [OOI] plus (100) [OOII components

grew commonly in the alloys with or without doped sulfur in which the growth

of (100) [OOI] components was dominant over that of (110) [OOI] in contrast to

Si-Fe alloy whose dominant component during growth was of a single (110) [OOI]

--orlentatlon.

(3) In view of the association of the growth behaviors in alloys to thecrystal growth or crystallization in other substances, the origination of liquid

phase along moving boundaries and thereupon the mode of grain growth in thepresence of a liquid phase were proposed.

The modes of grain growth in Al-Fe alloy sheet may eventually be attributed

to the presence of a liquid phase in the stage of, or in the temperature range

of grain growth and the effect of sulfur as the dopant should aiso be discussed

in the same situation. However, the prominent contribution by Taguchi andSakakura will also be one of the influential proofs for the growth of cube texture

in Al-Fe alioy2i).

For the confirmation of above conclusions especially on (3) term, the experi-

ments on other alloys entailing the similar energy process as well as the precise

plots of growth curves in AIFe alloys were undertaken with aflirmative results.

Acknowledgement

The authors acknowledge their indebtedness to Profs. K. Nishida, K, Matsubara

and T. Matsushita for the helpful advices and discussions,

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