Internal friction measurements in iron-nickel-carbon alloys

Scripta

METALLURGICA

Vol. 7, pp. 81-88, 1973 P r i n t e d in the U n i t e d States

INTERNAL

FRICTION

MEASUREMENTS

IRON-NICKEL-CARBON J.G.

van

der

University

Laan,

P.F.

(Received

Press,

IN

ALLOYS

Willemse

of T e c h n o l o g y

Pergamon

and

J.A.

Klostermann

Twente,

Enschede,

November

8, 1972)

the

Netherlands

Introduction In b . c . c . i r o n found

by

induced

with

internal

low

friction

diffusion

of

carbon

content,

measurements

interstitial

as

carbon

a "Snoek-peak" a result

atoms

in

of

the

can

be

stressoctahedral

sites(1). Scheil addition content At

et al.(2)

of n i c k e l of

ca.

has

been

Similar the

of

alloys

(carbon been

after

been

with

i. The

interactions

the

ordering

The between

also

and

of

the

at a n i c k e l

completely(3). internal and

the

friction

Forster(4).

Snoek-peak

and

for m a r t e n s i t i c

iron-

wt.pct).

by K o s t e r

et

al.(5)

in

low-

deformation.

nickel the

another

that

and

Scheil(2)

fading

0.5-1.0

of

peak;

described

content

structure

in a t e t r a g o n a l alpha

the are

observed

disappeared

by

measured

increasing

martensitic 2.

case

i.e.

plastic

this

has

however,

this

suggested(2,3)

height

al.(3)

lowers

200°C, in

a 200°C-peak,

has

steels

It has

ca.

iron

et

the p e a k

observations,

A 200°C-peak carbon

of

Jackson

the

measured

occurence

carbon

to

15 w t . p c t

a temperature

peak

and

that

the

content

carbon

decrease

may

atoms

be

with

due

of

the

Snoek-peak

to:

imperfections

in

the

or

stabilisation deformation

of

of

the

the

carbon

lattice

atoms

during

resulting the

gamma-

transformation. 200°-peak the

carbon

in the m a r t e n s i t i c

is s u g g e s t e d atoms

and

the

structure(2)

to a r i s e

from

dislocations or

deformation(5).

81

are

the

interaction

which

introduced

by

are

present

plastic

Inc

82

INTERNAL

The atoms

above

could

be

by C o t t r e l l ( 6 ) Plastic locking

FRICTION

mentioned

deformation

of

of the

Snoek-peak.

free

due

and

to d i f f u s i o n the

density

latter of FeNiC

Experimental

are

of

of the effect

give

composition in table

carbon

prep.

of

the F e N i C

alloys

used

the

in a r e t u r n

to study

this

the S n o e k - p e a k the d i s l o c a t i o n s . on the d i s l o c a t i o n

composition

of

the used

0.05

balance

2

25.0

0.05

balance

3

28.9

0.05

balance

4

3].5

0.05

balance

pct) The

subsequently damping

were

and

%Fe

produced

by

nlckel(99.999

as cast drawn

samples

into

wire

measurements

described

investigation

samples.

%C

specimens

in this

I

]6.1

The

of

toward

%Ni

pendulum

result

information

I

carbon.

an un-

I.

The

iron

time

then

procedure

The

The

proposed

increasing

investigation

some

carbon

martensite(8).

given

iron(99.998

cause

clouds should

with

interstitial could

Snoeklocking

would

This

decrease

TABLE

and

alloys

the present

the p o s s i b l e

and

7, No.

respectively.

the C o t t r e l l carbon.

Vol.

dislocations

and/or

Seeger(7)

of FeNiC from

interstitial

It is the object phenomenon

and

ALLOYS

between

of C o t t r e l l -

Schoeck

of d i s l o c a t i o n s

amount

Also

interaction

the result and

IN Fe-Ni-C

were

The

arc m e l t i n g

with

addition

homogenised

of 0.61

were

elswere(10).

argon pct)

in wt.pct.

mm

performed damping

for

diameter

of high

purity

of e u t e c t o i d a l 170 hr and

in a K ~ - t y p e ( 9 ) was m e a s u r e d

at

165 mm

ll50°C length.

torsion

at a f r e q u e n c y

I

Vol.

7, No.

]

of was

I

INTERNAL

Hz. The m a x i m u m -6 I0

elastic

FRICTION

strain

IN Fe-Ni-C ALLOYS

at the surface

83

of the specimen

Results The results with

16.1;

25;

900°C during

of the damping m e a s u r e m e n t s

28.9 and 31.5 wt.pct

5 min.

in purified

liquid N 2 are shown in fig. quenching

Ni resp.

Argon

1 (mean

of the F e N i C - a l l o y s after h e a t i n g

atmosphere

at

and q u e n c h i n g

time of the m e a s u r e m e n t s

in

after

I hr).

JD z 140~-

• v o •

12o~

FIG.

F e 16,11~Q 0 5 C Fe2~N,ooroC Fe29N~X~SC F e 31.,5~Q05C

Internal

i

8o~ 6O 40

1

friction

v.s.

temperature

of various

iron-nickel

carbon alloys

l hr after q u e n c h i n g

from

the g a m m a p h a s e ( 9 0 0 ° C )

in

liquid N2(-196°C)

1

2°tl '

I

,

30

2O

I

,

40

t

J

50

I

60

TEMPERATURE.°C

This

figure

indicates

that

do not

exhibit

(2,3).

The alloys with

damping

the alloys

a Snoek-peak,

which

with

]6.1

and 25 wt.pct

agrees with previous

29 and 31.5 wt.pct

Ni, however,

Ni

investigations show a small

peak at about 40°C

It is also evident in internal

The decreases

friction

Snoek-peak with

from figuTe

level b e t w e e n

observed

] that there

is a large d i f f e r e n c e

the alloys with

16 and

25 wt.pct

in the 29 and 31.5 pct Ni alloys

time as shown in figure

2.

Ni.

84

INTERNAL

FRICTION

7O

Z

IN F e - N i - C

ALLOYS

Vol.

7, No.

• Fe2gNiO.05C o FO31.SN~0.O5C

.=. Z

FIG.

4o

The

path

2

of the

internal

3C 2C 10

height

v.s.

time

After

5'o

w i r e was

the

disappearance

loaded

resulting

"in situ"

(finish

time,

as

reappeared

of the

with

in a d e f o r m a t i o n

Snoek-peak

0,05C

Fe31.5Ni TIME,MINUTES

the

peak

Fe29Ni

2'0

some

friction measured

a tensile

of about in both

illustrated

Snoek-peak

0.03

alloys,

in figure

3 for

of

29 w t . p c t

Internal

t = 0)

the

30 k g / m m 2,

but d i s a p p e a r e d the

is

quenching

alloys,

to this

FIG.

70

after

quenching

Due

8O

=

and

0,05C

in these

stress pct.

at 37°C

for

deformation again

3

friction

temperature

after

Ni alloy.

v.s.

for Fe29Ni

after a tensile stress 2 at d i f f e r e n t times

~ 6o

mm

straining.

50

40 I

20

=

I

30

,

I

,

40

I

TEMPERATURE

The

decrease

is shown

of

in fig.

the peak 4.

,

50

I

60

, °C

height

with

time

after

straining

at

37°C

0,05C of

30 kg/

after

i

Vol.

7, No.

i

INTERNAL

FRICTION

IN Fe-Ni-C A L L O Y S

85

Jo

z

70

.=F.

• Fe 29Ni 0.05C o Fe31.5N=0.0,~C

60

== ~- 4C Z

FIG.

3C

Internal

2C

37°C 1C

f r i c t i o n v.s.

2'o

3'o

I

,'0

J

50

60

70

time at

(maximum peak height)

a tensile

0

4

stress

after

of 30 k g / m m 2

at t = 0

TIMEMINUTES

The effect

of t e m p e r i n g

In this alloy, quenching,

and q u e n c h i n g also

~

which

a damping

is shown in fig.

does not peak

show a S n o e k - p e a k

is p r o d u c e d

in liquid N 2. Similar

this peak d i s a p p e a r s

80

5 for the 25 wt.pct after

by tempering

annealing

for

and

~hr at 400°C

to the peaks p r o d u c e d by d e f o r m a t i o n ,

after some time.

FIG.

Fe25N, 0.05C • o

5

HR

2 HRS )afte quencr~ng

Internal

70~-

rature

°i

f r i c t i o n v.s.

after

~hr at 400°C

__ 60

annealing

o

o

o

-

_

_

o

times(aging

during

measurements.) °

20

30

40

50

TEMPE RATURE, ° C

60

tempeduring

and q u e n c h i n g

liquid N 2 for different

I

50"~

4o i

Ni alloy.

in

aging

Snoek-peak

86

INTERNAL

FRICTION

IN F e - N i - C

ALLOYS

Vol.

7, No.

Discussion The

peaks

in 29 and after due

observed

31.5

wt.pct

tempering

to free

at 400°C

Ni alloys

I. A high

dislocation

practically

should

all

possess at

of

tion

the

ordering

carbon

cause

differences

resulting

nickel

to be The

iron

opinion

radii

of

to

locking

Snoek-locking.

seems

Ni a11oys not

unlikely

by

to

a change

in

twinning(ll).

by Jackson

likely,

randomly

of:

from massive

et al(3)

is tetragonal

due

that

the

to t r a n s f o r m a -

because

distributed

according

at

this

low

Ms-temperatures. the

sizes

This

occurs

16 and

phase,

3|.5 w t . p c t

is a c c o m p a n i e d

slip

is less

be

the o b s e r v e d

decrease of

the

the most

of

of

iron the

the

decrease

and nickel

atoms

could

octahedral

sites;

consequently

interstitial

atoms,

which

of

the peak

with

also

increasing

first

atoms

height

Harper

of carbon

measurements.

t

The

for

lack

time

could

dislocations.

the d i s l o c a t i o n showed atoms

of further

that

density

during

/

of the

peak

{-2L(~H) I/3

then This

may

be

evidences

caused

decrease according

strain

to d i s l o c a t i o n s

decrease

= exp. Qo

with

towards

to estimate

of Harper(8).

Q

explanation

likely.

in peak

carbon

a migration

damping

atoms, will

in the

density.

given

martensite

to the o b s e r v e d

the p o s s i b i l i t y theory

from

and/or

29 and

transition

result

in

content.

In our

diffusion

the

a transition

in a s t a b i l i s a t i o n

contributes

seems

and

the d i f f e r e n t

the

Ni

Snoek-relaxation a peak

martensite

by C o t t r e l l -

explanation

carbon

suggest

be

deformation

in 25 wt.pct

of such

the m a s s i v e

then

shear

of carbon

content

3. F i n a l l y

Ni

This

massive

the

could

and/or

3) and

strongly

dislocation

second

possible

formed

to Zener(12)

is true

wt.pct

martensite.

other

in

quenching

l and

absence

quenching,

a lower

the mode

rapidly

5) The

interstitials

28-30

after

(figs.

(in fig.

density

acicular

2. The

40°C

carbon.

after

supposition

because

ca.

alloys

interstitial

25 wt.pct

If this

at

Ni

aging

to

by:

(ADt/kT) 2/3}

the

of b.c.c.

be d e t e c t e d

is given

by

opens

by

I

Vol.

7,

No.

where

1

Qo

and

friction after

INTERNAL FRICTION IN F e - N i - C ALLOYS

Qt

peaks

A

is

describes

interstitial the

time the

the

the

minus

an a g i n g

density,

D is

are

K the

Boltzmann's

Using

this

the m a x i m u m

the b a c k g r o u n d

parameter

atom

of

at

t respectively,

interaction as

diffusion

in

a function

the

L is

the

energy

at

the

the

internal of

unknown

relation:

the

of

beginning

the

between of

coefficient

aging

U = Af(r,~)

a dislocation

position

of

absolute

and

dislocation which and

the

an

atom,

temperature

T,

constant.

equation

calculated Ii 7. ~0 and

values

87

and

the

above

mentioned

values

(8) we

have

from

the c u r v e s in fig. 4 a d i s l o c a t i o n d e n s i t y of about II -2 4.10 lines cm for the 29 and 31.5 pct Ni alloys

respectively. This

value

is

somewhat

observations(13,|4). determined measured

by

by

thin

other

A further The

results

It

higher

film

be

found

known

in e l e c t r o n t r a n s m i s s i o n

that

electronmicroscopy

methods

the

~s

dislocation

lower

than

density

those

(|5,16).

investigation

will

than

is h o w e v e r

of

published

this

problem

in due

course.

is b e i n g

carried

out.

Conclusions In m a r t e n s i t e and with

31.5

wt.pct

time

but

deformation The C atoms The

Fe-Ni-C

Ni

a Snoek-peak

can be m e a s u r e d

(29;

31.5

toward

the

of

has again

could

dislocations

decrease

with

0.05

been

wt.pct

found.

after

C and

The

peak

tempering

25;

29

disappears

(25 w t . p c t )

or

wt.pct).

disappearance

to e s t i m a t e

alloys

the

be

by w h i c h

peak

dislocation

due

height

to

the

diffusion

they

are

with

time

of

the

interstitial

locked. might

provide

a means

density.

Acknowledgement The

authors

criticizing for

would

like

the m a n u s c r i p t

experimental

assistance.

to and

thank

Prof.dr.ir.C.A.

helpful

diseussions

Verbraak and M r . A . M .

for Nijssen

88

INTERNAL

FRICTION

IN Fe-Ni-C ALLOYS

Vol.

REFERENCES. I. J.L.

Snoek,

2. E. Scheil, huttenw.

3. J.K.

Physica V I I I . 7 . 1 2

E. Wachtel

30.497

Jackson

and Pet.

4. F. Forster,

5. W. K~ster, 25.569

6. A.H.

und G. Gurbaxani,

Arch.

Eisen-

(1959).

and P.G.

Eng.

(1941).

Winchell,

230.216

Am.

Inst.

of Min. Met.

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Z. M e t a l l k d e .

29.109

(1939).

L. Bangert und R. Hahn, Arch.

Eisenhuttenw.

(1954).

Cottrel

and B.A.

Bilby,

Proc.

Phys.

Soc. A62.49

(1949).

7. G. Schoeck

and A. Seeger,

8

S. Harper,

Phys.

9

T.S.K~,

Phys.

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Rev. 83.709

Rev.

71.533

J.G.

van der Laan and A.M.

II

V.F.

Zackay,

12

C. Zener,

]3

C.M.

AIME

Reed

15. R.K. Ham,

]6. A.W.

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(to be published).

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et al.,

Phil.

Sleeswijk,

167.550

to the C r y s t a l l o g r a p h y

M c M i l l a n N.Y.

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5.485

(1971).

Scripta Met.

Mag.

John Wiley

Ir. and St. Div.

sitic T r a n s f o r m a t i o n s .

]4. R.P.

(|951).

High-Strength Materials,

Trans.

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|0

Wayman,

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of M a r t e n -

7, No.

i