effect of columbium and vanadium on the weldability of hsla steels
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8/10/2019 Effect of Columbium and Vanadium on the Weldability of HSLA Steels
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E f f e c t o f C o l u m b i u m a n d V a n a d i u m
on the Weldab i l i t y o f HSLA Stee ls
Excellent low-temperature HAZ and weld-metal
toughness can be obtained in a variety of HSL A steels
containing Cb and V
BY E. G. SIGNES A N D J. C. BAKER
MA R Y . A co mp r e h e n s i ve s t u dy
h i g h -
e ta l toughness.
Results were based on a series of 500
Si-Al-ki I led low -su l fur stee ls
c o n
e looked at com pos i t i ons i n wh ich
respect ive ly.
Much of the data was sta t ist ica l ly
Equa t ions were deve loped
dict ed as a func
Cb and V. Me ta l log raph y
In genera l , goo d we ld -m e ta l and
The main f ind ings of the study
1.
HAZ toughnes s increased w i th
presented at the AWS 60th Annual
2-6,
1979
G. 5IGNES is a Research
Engineer—Prod
I
C
BAKER is Research
Metallurgy, Bethlehem
Corporation, Homer Research Labora
2. Th ree d i f fe ren t e lec t rode / f l ux
co m b i n a t i o n s g a ve g o o d w e l d -m e t a l
tough ness in most cases. At lo w C
leve ls a T i -B e lec t rode pro duc ed
excep t iona l l y tough we ld me ta l fo r a l l
microa l l oy comb ina t ions, even in s tee l
conta in ing 0 .15% Cb.
M a t e r i a l s a n d W e l d i n g
P r o ced u r es
The composi t ions o f a l l p la tes tested
are give n in Table 1 . The f i rst 15 heats
l isted in this table were chosen to f i t a
pa r t i a l th ree - leve l fac to r ia l expe r imen
ta l des ign , known as a Box-Behnken
des ign . '
These heats were based on
variat ions in C, Cb and V levels. The
levels for the f i f teen heats were:
C
( )
0.18
0.13
0.08
Cb ( )
0.06
0.03
Trace
V ( )
0 .10
0.05
Trace
Heats 16 and 17 in Table 1 also fall
w i th in o r c lose to the above compos i
t ion ranges but were not part of the
factorial design. Heats 18 and 19
conta ined Cb contents in excess of
0.06%.
A l l heats were a i r - i n duc t ion - me l ted
500 lb (225 kg) laboratory heats. Also,
al l heats were slabbed to a thickness of
4 in. (102 m m ), rehe ated to 2000 F
(1090 C), and contro l -ro l led to in.
(19 mm) p la te over the temperature
range of 1620 to 1300 F (880 to 700
C).
Referr ing to Table 2 , three consum
ab le comb ina t ions were used :
1.
A 0.5% N i -0 .5% M o e lect ro de
(coded 44) selected because earl ier
test ing had shown that i t produces
sl ight ly bet te r toughn ess than a 0 .5%
Mo e lect rode and substant ia l ly bet ter
toughne ss than a st ra ight C- Mn e lec
t r ode .
Th is e lect rode was used wi th an
Table
1 —Plate
Composit ion, %
Heat' Code Mn Cb
I
2
3
4
5
6
7
8
9
10
11
12
13
14
15
16
17
18
19
112
123
132
121
211
213
233
231
312
323
332
321
M 1
M 2
M 3
131
333
141
151
0.085
0.078
0.070
0.083
0.14
0.13
0.15
0.14
0.18
0.18
0.19
0.24
0.12
0.13
0.14
0.077
0.19
0.077
0.089
1.24
1.49
1.37
1.41
1.47
1.36
1.45
1.25
1.51
1.39
1.45
1.45
1.40
1.40
1.44
1.41
1.44
1.41
1.43
< 0.005
0.028
0.059
0.027
< 0.005
< 0.005
0.056
0.059
< 0.005
0.028
0.068
0.028
0.031
0.028
0.027
0.055
0.053
0.12
0.15
0.047
0.095
0.048
0.002
< 0.002
0.10
0.10
0.002
0.052
0.093
0.052
< 0.002
0.048
0.050
0.050
< 0.002
0.11
< 0.002
0.002
A l l h e a l s c o n t a i n £ 0 .01 % P, 0 .004/0.006% S, 0 .20/0 .30% Si , 0 .025/0.040 %
A l,
0 .005/0.008% O a n d 0.007/0.011 N.
W E L D I N G R E SE A RC H S U P P LE M E N T I 179-s
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Table 2-C omp osit ions of Submerged Arc W elding Consumables, %
Electrode compositions
Code
44
120
TB
Code
851
0091
121
' CaO +
Type
0.5%Ni-0.5%Mo
2.5%Ni-0.5%Mo-0.5%Cr
0.03%Ti-B-0.25
o/
oMo
CaF.. + MgO + K.O + Na,0 + I
C
0.14
0.07
0.059
C
0.002
0.190
0.350
i ( M nO + 1
SiO, + 2 (ALO, + TiO + ZrO.)
M n
2.09
1.55
1.32
S iO,
42.8
36.0
10.7
eO)
S
0.011
0.008
0.006
A L O ,
2.6
3.2
17.3
P
0.019
0.006
0.003
Fe..O,
0.39
0.20
1.90
Si
0.05
0.35
0.03
C a O
37.5
46.3
6.6
Al
0.023
0.025
0.024
M o
0.49
0.55
0.25
N i
0.60
2.40
0.06
F l ux c om pos i t i ons
M g O
0.40
0.36
31.70
M n O
0.41
0.14
1.10
T i O ,
11.50
4.40
0.86
Ti
-
-
0.03
N a . O
0.05
5.10
0.78
li
-
-
0.010
CaF.,
4.5
9.8
24.1
Cr
-
0.45
-
Bas ic it y ind ex ' '
0.85
1.55
3.13
ac id f lux ( coded 851) because more-
basic f luxes d id not produce bet ter
t o u gh n e s s w i t h o u r we ld in g p r o c e
dures.
2. A 2 .5% Ni -0 .5% Mo-0 .5% Cr e lec
t rode ( coded 120) used in combina t ion
with a less ac id ic f lux (coded 0091) .
3 . A 0 .03% T i -B-0 .25% M o e lec t rod e
(coded TB) used wi th a bas ic f lux
(coded 121) .
A l l we ld i n g wa s d o n e u s in g a Sc o t t -
c o n n e c t e d t a n d e m A C / A C s u b
merged-arc system. One pass per s ide
wa s d e p o s i t e d i n t o a d o u b le - V j o i n t .
Except where o therwise no ted , t he
p la tes we re we ld ed wi th a hea t inpu t
of 75 k j / i n . (3 .0 k j /m m ) . A few p la tes
we r e we ld e d w i t h 4 5 a n d 1 0 0 k j / i n .
(1 .8 and 3 .9 k ) /mm) . These we ld ing
proced ures , w h ic h resu l t ed in d i l u
t ions o f 60-65%, had the fo l low ing
parameters :
Lead head
Trai l head
Current,
A
950
700
Voltage,
V
30
35
Table 3—Data Used in Statistical Analysis
Toughness
propert ies '
,
at —50 F (—46 C)
Co
C
Box -Behnk
0.08
0.08
0.07
0.08
0.14
0.13
0.15
0.14
0.18
0.18
0.19
0.24
0.12
0.13
0.14
A d d i t i o n a l
0.08
0.19
m
pos i t i on ,
Cb
en Heats :
0
0.03
0.06
0.03
0
0
0.06
0.06
0
0.03
0.07
0.03
0.03
0.03
0.03
Heats
0.06
0.05
%
V
0.05
0.10
0.05
0
0
0.10
0.10
0
0.05
0.09
0.05
0
0.05
0.05
0.05
0
0.11
Code
112
123
132
121
211
213
233
231
312
323
332
321
M l
M 2
M 3
131
333
Tens i le
YS
ksi
(MPa)
54.3
(374)
76.8
(529)
70.4
(485)
64.3
(443)
54.6
(376)
63.4
(437)
69.5
(479)
61.2
(422)
64.7
(446)
75.5
(521)
68.9
(475)
68.0
(469)
68.8
(474)
65.2
(454)
67.3
(464)
69.7
(481)
77.0
(531)
proper t ies
1
UTS
ksi
(MPa)
67.7
(467)
82.1
(566)
76.8
(529)
72.5
(500)
73.6
(507)
79.3
(547)
84.0
(579)
74.3
(512)
84.1
(580)
90.3
(623)
87.3
(602)
87.8
(605)
78.9
(544)
77.9
(537)
81.6
(563)
76.6
(528)
94.6
(652)
Base meta l CVN,
I t - l b
(I)
67.5
(91.5)
65.5
(88.8)
104.5
(141.7)
83.0
(112.5)
42.5
(57.6)
35.0
(47.5)
40.0
(4.7)
56.5
(76.6)
35.0
(47.5)
34.0
(46.1)
43.0
(58.3)
29.0
(39.3)
71.5
(97.0)
63.0
(85.4)
61.5
(83.4)
125.5
(170.2)
43.5
(59.0)
H A Z C V N ,
f t - l b
(I)
45.7
(62.0)
40.0
(54.2)
57.7
(78.2)
46.8
(63.5)
29.0
(39.3)
42.0
(57.0)
15.0
(20.3)
34.5
(46.7)
47.0
(63.7)
13.0
(17.6)
8.5
(11.5)
22.5
(30.5)
32.5
(44.1)
10.7
(14.5)
22.0
(29.8)
72.1
(97.8)
11.1
(15.1)
4 4 /8 5 1 ,
f t - l b
(I)
50.0
(67.8)
32.0
(43.4)
28.0
(33.0)
30.5
(41.4)
32.0
(43.4)
45.5
(61.7)
50.5
(68.5)
39.0
(52.9)
42.0
(57.0)
49.3
(66.9)
29.0
(39.3)
31.3
(42.4)
61.5
(83.4)
43.0
(58.3)
43.0
(58.3)
102.3
(138.7)
22.4
(30.4)
We l d m e t a l
120 /0091 ,
f t - l b
(I)
60.7
(82.3)
82.0
(111.2)
52.7
(71.5)
87.5
(118.7)
84.0
(113.9)
88.5
(120.0)
28.8
(39.1)
77.5
(105.1)
63.0
(85.4)
29.2
(39.6)
52.7
(71.5)
30.7
(41.6)
52.7
(71.5)
46.0
(62.4)
54.3
(73.6)
96.0
(130.2)
42.0
(57.0)
T B /
12 1
f t - l b
(1)
115.0
(155.9)
118.3
(160.4)
138.0
(187.1)
139.0
(188.4)
49.0
(66.4)
66.3
(89.9)
40.0
(54.2)
77.3
(104.8)
15.4
(20.9)
60.3
(81.8)
95.3
(129.2)
1.5
(2.0)
74.7
(101.3)
64.3
(87.2)
59.3
(80.4)
154.0
(208.8)
124.0
(168.1)
YS—Yield st rength; UTS—ultimate tensile strength.
CVN— Chapry V—notch; HAZ—heat-affected zone.
180-s I JUN E 1979
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4—Results
of Multiple Linear Regression Analysis
B,(%
Cb) +
B,(%
V) +
B,,(%
C
3
) + B.,.,{ Cb
3
) +
B
M
(%
V
3
)
4- B,,( C x % Cb ) I B„(% C x % V) 4-
B
M
(%
Cb x % V)
(4) -50 H HAZ - CVN energy at -50F (-46C)
(5) -5044 weld metal (44/851) CVN energy at -50F (-46C)
-50F (-46C) (6) -501 20 we ld metal (120/0091) CVN energy at -50 F (46C)
(7) -50TB weld metal
(TB/121)
CVN energy at -50F (-46C)
Coeff icients of above equat ion'
U n i t s
ksi
ksi
f t - l b
f t - l b
f t - l b
f t - l b
f t - l b
R
.9461
.9663
.9752
.9651
.6147
.9022
.9600
B„
61.75
66.98
157.0
99.09
Not inc
96.89
421.8
SErr
3.188
2.717
8.838
7.225
21.35
13.42
19.08
B,
- 1 6 8 . 9
- 4 0 . 6 6
- 1 2 2 2
- 846 . 2
B
2
674.3
347.8
1172
209.4
B„
B,, B
2
,
57.53 748.6 -5 27 7
14.22 542.6 -21 21
- 323 . 3 2765 - 47 01
-24 5.5 2680 11720
uded s i nc e ana l y s i s s howed no m ean i ng f u l c o r re l a t i on
- 18 . 18
- 3 9 1 5
- 4 3 0 . 3
- 1 5 4 4
- 68 5 . 0 - 933 . 9 8253
-1 47 3 8306 6550
Sta t i s t i ca l parameters
F
6.643
10.94
15.12
10.56
0.47
3.40
9.14
P
0.0103
0.0023
0.0008
0.0026
0.8540
0.0602
0.0040
C o r r e l a t i o n
1 0
G o o d
Exce l len t
Exce l len t
Exce l len t
N o n e
Fair
Exce l len t
B„
8.8
41.3
- 3 0 8 5
1291
6588
1963
B„
- 1 4 2 1
- 1 1 2 9
- 3 6 4 9
- 6 3 7 1
671.5
12800
B«
473.4
547.3
3964
1684
1198
10743
B,;,
- 485 . 2
95.30
- 1 6 4 2
- 5 1 5 4
- 9 3 0 8
- 4 0 8 6
convert to SI units, multiply coefficients for: ksi X 6.895 to get MPa and ft- lb X
1.356
to get J.
correlation coefficient; SErr—standard error of estimate;
F—F-ratio; P—Probability
that the variance can be explained by change.
define d as: Excellent: P < 0.01 Fair: 0.05 < P£0.1 5
Good:
0.01 < P £ 0 . 0 5
Poor:
0.15 < P
Tensi le, Charpy and hardness tests
(12.8 mm) tensi le specimens were
Charpy tes t ing o f base meta l , HAZ
we ld - m e t a l s p e c im e n s we r e t a k
we ld .
0 F (—46 C) . To inc lud e as mu ch of
Va
in . (1.5 m m)
wh ere the no tch inc lu ded 50%
ld me ta l and 50% HA Z. A l l H AZ and
Hardness t raverses of selected welds
A number o f we lds were s tud ied
Th e q u a n t i t a t i v e o p t i c a l
s is was don e w i th a TAS ( Tex
An a ly z in g Sy s te m , a q u a n t i t a t i v e
s and Discus sion
Th is sec t ion dea ls ma in ly w i t h t he
chemis t r y e f f ec t s on the mechan ica l
p roper t ies o f base meta l , HAZ and
weld metal of heats made to the Box-
Behnken des ign . Chemis t r y e f f ec t s in
the st ra ight -Cb heats as wel l as the
e f fec t s o f coo l ing ra te on no tch tough
ness are then discussed.
Heats in Box-Behnken Design
A mu l t ip le l inear regress ion p rogram
was employed to de te rm ine the re la
t ionsh ip o f seven dependent var iab les
to C, Cb and V. These var iables were:
1. Base-metal y ie ld s t rength (YS) .
2. Base-meta l u l t im ate tens i le
st rength (UTS) .
3 . Base-meta l Charpy V-n o tch
(CVN ) energy at -5 0 F ( - 46 C) .
4. HAZ CVN e n e r gy a t - 5 0 F ( - 4 6
Q.
5 . W e ld - m e t a l CVN e n e r gy a t - 5 0 F
( -46 C) f o r 44/851 electrode/flux
c o m b i n a t i o n .
6 . W e ld - m e t a l CVN e n e r gy a t - 5 0 F
( -46 C) f o r 120 /0091 e lec t rode / f lux
c o m b i n a t i o n .
7 . W e ld - m e t a l CVN e n e r gy at - 5 0 F
( -46 C) f o r TB/121 e lec t rode / f lux
c o m b i n a t i o n .
The equat ion express ing the re la
t i o n s h ip wa s g i v e n t h e f o l l o w in g
f o r m :
De pe nde nt Var iab le = B„ + B,
+ B., (C b) 4- B, (V) + B,, (C
3
) +
(Cb
3
) 4- B„ (V
3
) 4- B„ (C x Cb) 4-
(C x V) + B.„ (Cb x V)
(C)
wh ere C, Cb , and V = w t % of C, Cb
and V in the base metal .
Two add i t iona l hea ts were
made-0.08% C, 0.06% Cb, 0% V, and
0.18% C, 0.06% Cb and 0.10% V - o n the
basis of the or ig inal analys is of the 15
heats in t he Box-Behnken des ign . The
data ob ta ined f rom these hea ts were
combined wi th t hose o f t he 15 o r ig ina l
heats.
Tab le 3 represen ts the co mb ine d
data; their ana lys is is g iv en in Table 4,
wh ich p resen ts t he coe f f ic ien ts f o r
each equat ion and also several s tat is t i
cal parameters associated with
t h e m— n a me l y ,
t h e m u l t i p l e c o r r e l a
t ion coe f f i c ien t , t he s tandard e r ro r o f
es t imate , t he F- ra tio , and the f rac t ion
o f t he var iance exp la inab le by
chance .
In the last column of Table 4, cor re
la t ion is de f ine d as: ex ce l le n t i f
P < 0.0 1, i.e., if > 99% of the var iance
can be exp la ined by the C, Cb and V
le v e l s ; go o d fo r 0.01 < P < 0.05; and
fa ir for 0.05 < P < 0.15. In one case,
the toughness o f t he 44 /851 we ld
meta l , t here was no mean ing fu l co r re
la t ion , P be ing 0 .85. Conse que nt ly , t he
e le m e n t s a d d e d f r o m t h e we ld in g
c o n s u m a b le s a n d / o r t h e i r i n t e r a c t i o n
wi th t he base meta l were p robab ly
more s ign i f i can t t han the base-p la te
c o m p o s i t i o n .
For easier understanding, a ser ies of
curves based on the regression data
we r e p lo t t e d . For ea c h d e p e n d e n t var i
able, n ine curves of predic ted isolevels
W E L D I N G R E S EA R CH S U P P L E M E N T I
181-s
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l HAZ
-fe-;'
;
*f l
,..*;: ;-^».y«',....*, .- -; . <.-^..,r.r .
,:
3 >
^ A ~**
. ^ ^ t n * i ^
-**
1
;;
<kmm
y - - ~ * > > . . v ; •
i
w:><s
,
u
3
-w(T^;
;
.
4—HAZ microstructures of tow an d
0.06 Cb and
A-heat
132
(0.07
C, 58 it-lb at
F); B-heat 332 (0.19 C, 8 ft-lb at
Nital etch, X250 (reduced
33
on
t c o n t a in e d p r e d o m i
the b a in i t e co l ony s ize
and the s t ruc tu re becam e
re la th l ik e, as seen in Fig. 4 w hi ch
2- bo th a t a 0 .06% Cb an d 0 .05% V
250
o
>
<n
tn
UJ
Q
or
<
X
N
<
?
-D
i
X
<
^
240
230
2 2 0
2 I 0
?or
I 9 0
Legend
0.08 %C heats
0.13 % C heats
(D
V///A
0.18 %C heats
IO 20 30 40 50 60
HAZ TOUGHNESS, f t - lb at
70 80
- 5 0 F ( - 4 6 C)
Fig.
5—HAZ
toughness as a function of max imum hardness (multiply ft-lb by
1.356
to get I)
level but wi th C conte nts of 0.07% and
0.19%, respec t ive ly . On the o th er han d,
wh en the C is cons tan t , t he var ia t ion in
the Cb and V levels has l i t t le in f luence
on the m ic ros t ruc tu re .
Accord ing to var ious inves t iga to rs ,
when coo l ing ra tes a re re la t ive ly s low
so tha t g ra in coarsen ing and p rec ip i t a
t ion take p lace, e i ther Cb or V can
decease the HAZ toughness .
C o n
verse ly , when coo l ing ra tes a re re la
t ive ly fast, the effe ct o f C b or V 'is to
impro ve the HA Z toug hness as a resu lt
o f g ra in re f inem ent and p roe u te c to id
fer r i te suppression. P.H.M. Har t
et al.
summar ized several of these studies
cover ing a range o f coo l ing ra tes and
Cb , V and o ther a l loy ing add i t ions .
3
O u r c o o l i n g t im e o f 25 s e c o n d s f r o m
800 to 500 C (1472 to 932 F) result ing
f rom the 75
k j / i n .
(3.0 k j /mm) c o n d i
t ions was near the fast end of the
repor ted range . A t t h is coo l ing ra te ,
bu t depend ing on the C leve l , e i t her
Cb or V inc reased the HAZ toughness
in our s tudy . However , in con t ras t t o
Har t , w ho repor te d tha t V was m ore
e f fec t ive as t he C con te n t was
lo we r e d , we f o u n d t h a t V wa s m o r e
ef fect ive at a h igher C-0.18%. Cb was
more e f f ec t ive a t a lower C
lev-
e l - 0 . 0 8 % .
Ext ract ion repl icas and th in f i lms
examined in t he TEM d id no t show
any p rec ip i t a tes t ha t wou ld exp la in t he
HAZ toughness var ia t ions . L ikewise ,
0 1 0
120/0091
Weld Meta l
Toughness, f t -l b a t - 5 0 F
C=0.08 %
0 1 0
120/0091 Weld Metal Toughness,ft-lb a t - 5 0 F
C =
0 . 1 8 %
0.03 006
COLUMBIUM
6-CVN
energy
levels
at -50
F
(-46
C)
in ft-lb ol
120/0091
weld
0.08
C (multiply by
1.356
to get I)
0 0 3 0 0 6
COLUMBIUM
Fig. 7-CVN
energy levels at -50
F
(-46
C)
in ft-lb ol 120/0091 weld
metal for
0.18
C (multiply by
1.356
to get I)
W E L D I N G R E S EA R C H S U P P L E M E N T I 183-s
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TB/121 Weld M etal Tou ghn ess, f t - lb at -
C = 0 . 0 8 %
5 0 F
TB/121 Weld Metal
Toughness,ft-lb
C = 0 1 8 %
a t - 5 0 F
2
a
<
<
>
0 0
0.03
COLUMBIUM
0.06
0
03
CO L UM BI UM
0.06
Fig.
8-CVN
energy levels
at -50
F
(-46
C )
in
ft-lb
of
TB/121 weld
metal lor
0.08
C (m ultiply
by 1.356 to
get I)
Fig.
9-CV N energy
levels
at -50F (-46
C)
in
it-lb
of
TB/121 weld
metal
for 0.18
C (m ultiply
by
1.356
to
get I)
no Cb-
or
V-be ar ing p rec ip i t a tes we re
f o u n d
on
f rac tu re sur faces w he n
the
SEM
was
used . Ho we ver , t ha t p re c ip i
t a t ion was o c c u r r i n g in the HAZ can
be in fe r red f rom
the
c o m p a r i s o n
of
m a x i m u m
HAZ
h a rd n e ss w i t h t o u g h -
§:m^'MM^M
Fig.
10-Weld-metal
structures
of
steel
132
(0.07
C, 0.06% Cb,
0.05
V):
A-welded
with
120/0091
(53 ft-lb
at -50 F);
B-welded
with
44/851
(28 ft-lb
at -50
F). Nital etch,
X50
(reduced
20
on
reproduction)
ness (Fig.
5),
wh e r e t h e r e
is a
cor re la
t i o n ,
e v e n w i t h i n l i k e
C
levels .
As for
the base plates, we f o u n d no cor re la
t ion of hardness w i th t oughness .
Canadian researchers
di d
f ind p re
c i p i t a t i o n
in the
f o rm
of CbC and
V(C,N) in the
HAZ
of
a
0.09% C b
and
a
0.09% V s tee l , r espec t ive ly , but o n l y in
very s lowly coo led we lds .
3
On the
other han d, t hey fou nd tha t
the
smal l
size
of the
HAZ
in
we ld s p r o d u c e d
by
c o n d i t i o n s s im i l a r to ours p resen ted
in s u r m o u n t a b le s a m p l i n g p r o b le m s .
Weld Metal.
The
r e l a t i o n s h ip
of
t o u gh n e s s to base-me ta l che mis t r y
was stat is t ica l ly re levant for the 120/
0091
and
T B / 12 1 c o n s u m a b l e c o m b i
na t ions
bu t not for the 4 4 / 8 5 1 .
W i t h
one except ion , t oughness us ing 44 /851
c o m b in a t i o n r a n ge d f r o m
25
to
50
f t - lb
(34 to
68 ))
at - 5 0 F
( -46
C ). In al l cases
e i t her
one or the
o t h e r c o n s u m a b le
c o m b in a t i o n p r o d u c e d b e t t e r r e s u l t s
than did the 44 /851 .
W e ld - m e t a l t o u gh n e s s u s in g
120/
0091 decreased w i th C.
For all
C levels ,
t he re la t ionsh ip be tween toughness
and the m ic r o a l l o y i n g e le m e n t s was
s im i l a r : m a x im u m t o u gh n e s s o c c u r r e d
at e i ther h igh
Cb or
h i gh
V,
whereas
m in im u m t o u gh n e s s o c c u r r e d at h igh
Cb + h i gh V ( spec i f i ca l ly ,
0.06%
Cb,
0.08%
V).
Figures
6 and 7
show these
re la t ionsh ips
for 0.08 and 0.18% C
respec t ive ly .
CVN
energ y us ing th is
c o m b in a t i o n v a r i e d f r o m 35 to
95
f t - lb
(47 to
128
|).
W e ld - m e t a l t o u gh n e s s u s in g TB / 1 2 1
s h o w e d
a
c o m p le x r e l a t i o n s h ip
be
t w e e n
C and the t wo
m ic r o a l l o y i n g
e le m e n t s .
As
seen
in
Fig.
8, all
t o u g h
nesses at 0.08%
C
we r e e x c e l l e n t ( > 90
f t - lb [122 |] at - 5 0 F [- 46 CJ), w i t h
t o u gh n e s s im p r o v in g as Cb and V we r e
decreased.
For
h i gh
C,
h o we v e r , s u b
s tan t ia l amounts
of V
a n d / o r Cb , p r e f
erably b o t h , are n e e d e d to get go o d
we ld - m e t a l t o u gh n e s s ,
as
s h o w n in Fig
9, w h ic h p resen ts an o p p o s i t e t r e n d
f r o m Fig.
8.
The fact that toughness at
0.18%
C
var ies f rom 90 f t - l b (122 J) d o w n to
v i r t ua l ly zero under l ines
the
i m p o r
tance
of the
m ic ro a l loy leve ls
for
h igh
C s i tuat ions. These resul ts indicate that
TB/121 we lds are a f f ec ted by d i l u t i o n
more than we lds made wi th t rad i t iona l
iM^uM^AKC-AA€A-
fe-ii,/ '':>sV
;
-'r;:^
r?>
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|pg
A:^:^^.A--y
>
,:
l&yA-^ M
, , f » > J
-•••>
•
Ar.
•
.yyy-yA ^Aru-;xA A '^
.- .Ay
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' ''--*:';
iiZ'l »\P
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.-T:< . i . v
...K,, ,V. ' ' .
»\ . \ > W
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:
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Fig. 77—Weld-metal
structures
of
steel
132
(0.07
C,
0.06
Cb.
0.05
V):
A-welded
with 44/851 (28 ft-lb
at -50
F); B-welded
with TB/121
(138 It-lb at -50 F) .
Nital etch,
X500
184-s I |UN E
1979
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g s u ch ti t a n i u m / b o r o n c o n s u m
W e ld - m e t a l m i c r o s t r u c t u r e s we r e
The presence o f p roeu tec to id f e r r i t e
kn ow n as ve in ing—Fig . 10A. To
to de te rm ine % ve in ing in
owe d no ve in ing—Fig . 10B.
The s t ruc tu res be tween the p roeu
Cb , 0.05% V) we ld ed w it h 4 4/851
0 F (38 and 187 J at -4 6 C) , respec
A l th ou gh the t rend fo r a wh i le had
ess that a go od w el d metal
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13—M-A phase in two welds in steel 132
C, 0.06 Cb, 0.05 V): A-welded
It-lb
at -50 F); B-welded
(138 ft-lb at -50 F). 10
sodi
metabisulfite, x 1000 (reduced 20 on
Fig. 12— Two weld metal structures pro
duced with TB/121: A-steel 312 (15 ft-lb at
-50 F); B-steel 332 (95 ft-lb at -50 F). Nital
etch, X500
t ion is by no means that s im ple.
Gar land and K i r kwood had a lso made
a s im i la r po in t .
3
Some inves t iga to rs have cons idered
that the coarsening of ac icular fer r i te
may be a cause of poor tough ness .
Figure 12 shows two st ructures in
wh ich la th s ize may be a con t r ibu t ing
fac to r t o t oughness . However , t he
quant i tat ive analys is of la th s ize is not
pract ical for such st ructures.
Th e m a r t e n s i t e / a u s t e n i t e m ic r o c o n -
s t i t uen t kn ow n as M-A has been
repor ted to be de t r im enta l t o w e l d -
meta l t oughness .
5
For th is reason, we
examined we ld meta l samples to de
t e r m in e t h e a m o u n t o f M - A m ic r o -
phase present . The samples were
examined a t
X1000
a f t e r e t ch ing w i th
sod ium metab isu l f i t e , and the M-A
feature is d is cer nib le in Fig. 13, w hi ch
has the same weld metals as those
sho wn in F ig . 11 . As de te rm ine d by the
TAS,
the percentag es of the M-A phase
in several welds (Table 5) point to a
re la t ion be tween th is phase and
toughness— spec i f i ca l ly , t he more M-A
the lower t he toughness .
Straight-Cb Steels
F o u r s t e el s w e r e m a d e w i t h C b a s
t h e o n l y m i c r o a l l o y i n g
e lement—Table
6 . S t r e n g t h a n d b o t h t h e b a s e m e t a l
a n d H A Z t o u g h n e s s e s w e r e m a x i m i z e d
i n t h e 0 .0 6 - 0 . 1 2 % C b r a n g e , w h e r e a s
w e l d - m e t a l t o u g h n e s s w a s be s t a t
a b o u t 0 . 0 6 % C b .
M e t a l l o g r a p h i c e x a m i n a t i o n s
s h o w e d v e r y l i t tl e d i f f e r e n c e a m o n g
t h e w e l d m e t a l a n d H A Z m i c r o s t r u c
t u r e s o f l o w - c a r b o n
s t ra igh t -Cb
s tee ls
o f v a r y i n g t o u g h n e s s . A s t h e r e s u l t s
i n d i c a t e , w i t h t h e p r o p e r c o n s u m a b l e s
a n d w e l d i n g c o n d i t i o n s , w e l d m e t a l
t o u g h n e s s s h o u l d n o t b e a l i m i t i n g
f a c t o r e v e n i n t h e v e r y h i g h - C b
s t ee l s .
E f fec t o f Weld Coo l ing Rate on
T oug hnes s
T a b l e 7 s h o w s t h a t a d e c r e a s e i n
c o o l i n g r a te d u e to in c r e a s i n g h e a t
i n p u t g e n e r a l l y l ea d s t o p o o r e r t o u g h
n e ss i n t h e H A Z a n d w e l d m e t a l , a n
e f f e c t g e n e r a l l y n o t e d i n t h e l i t e r a t u r e .
I n t h e H A Z t h i s d e c r e a s e d t o u g h n e s s i s
a s s o c i a t e d w i t h a c o a r s e - g r a i n e d r e
g i o n t h a t is b o t h w i d e r a n d c o a r s e r , t h e
s l o w e r t h e c o o l i n g r a t e .
A l l c o a r s e - g r a i n e d H A Z a r e a s o b
s e r v e d w e r e p r e d o m i n a n t l y b a i n i t e ,
w i t h p r e s e n c e o r a b s e n c e o f m a r t e n
s i t e a n d o v e r a l l c o a r s e n e s s b e i n g t h e
m a i n d i s t i n g u i s h i n g f e a t u r e s . F o r s t e e l
2 3 1 ( 0 .1 4 % C , 0 . 0 6 % C b , 0 % V ) w e l d e d
a t 45 and 100 k j / i n . (1 .8 and 3 .0 k ) /
m m ) , F i g . 1 4 s h o w s a ty p i c a l c o a r s e
g r a i n e d r e g i o n . A t 1 0 0 k j / i n . (3.0 k | /
m m ) t h e s t r u c t u r e is p r e d o m i n a n t l y
u p p e r b a i n i t e , w h e r e a s a t 4 5
k j / i n .
(1 .8
k j / m m ) a m i x t u r e o f l o w e r b a i n i t e a n d
m a r t e n s i t e is f o r m e d .
A m i c r o s c o p i c e x a m i n a t i o n i n d i
c a t e d t h a t t h e a m o u n t o f p r o e u t e c t o i d
f e r r i t e d i d i n c r e a s e , a l t h o u g h t h e T A S
w a s u n a b l e t o d e t e c t a s i g n i f i c a n t
i n c r e a s e i n t h e a m o u n t o f v e i n i n g o f
1 0 0 k j / i n . ( 3 .0 k j / m m ) w e l d s as
c o m p a r e d w i t h 4 5
k j / i n
(1 .8
k j / m m )
w e l d s . A l s o , t h e s t r u c t u r e b e c a m e
c o a r s e r a t s l o w e r c o o l i n g r a t e s .
T h e s e p h e n o m e n a c a n b e s e e n in
F i g u r e 1 5 , w h i c h s h o w s t h e s t r u c t u r e
o f s t ee l 151 (0 . 09 % C , 0 . 15% C b , 0% V )
w e l d m e t a l w e l d e d w i t h T B / 1 2 1 a t 4 5
a n d 1 0 0 k j / i n . ( 1 . 8 a n d 3.0 k j / m m ) .
T ab l e 5—M-A M i c roph as e i n We l d M e t a l as De t e rm i ned by T A S
(%)—Comparison
w i t h
T oug hnes s
Base
M e t a l
132
132
132
332
312
C o m p o s i t i o n ,
C
0.07
0.07
0.07
0.19
0.18
Cb
0.06
0.06
0.06
0.07
0
%
V
0.05
0.05
0.05
0.05
0.05
W e l d
c ons um ab l es
44/851
120/0091
TB/121
TB/121
T B / 121
M-A, %
11.7
11.5
6.5
5.9
13.9
C V N ,
f t - lb ( ] )
al
- 5 0 F ( - 4 6 C )
28 (38)
53 (72)
138
(187)
95 (129)
15 (20)
W E L D I N G R E S E A R C H S U P P L E M E N T I 1 8 5 - s
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T ab l e
6—Properties
o f S t ra igh t -Cb Heats
f t - l b ( | ) at -5 0 F ( - 46 C)
C o d e
121
131
141
151
' YS-yield si
Comp
C
0.08
0.08
0.08
0.09
rength; UTS-
os i t i on , %
C b
0.03
0.06
0.12
0.15
ultimate tensile
YS,
ksi '
64.3
69.7
71.0
66.5
UTS, k s i
72.5
76.6
77.0
74.3
slreng h; ksi x 6.895 - MP a.
Base metal
83 (112)
125 (169)
105 (142)
95 (129)
HA Z
47 (64)
59 (80)
77 (104)
70 (95)
44/851
30 (41)
102 (138)
28 (38)
32 (43)
W e l d M e t a l
120/0091
87
(118)
96 (130)
62 (84)
29 (40)
TB/121
139
(188)
154 (209)
62 (84)
68 (92)
Tab le
7—CVN
Energy as a Func t ion o f Heat I np ut
C o m p o s i t i o n ,
Code C Cb
y
211
0.14 0 0.00
213 0.13 0 0.10
231 0.14 0.06 0
M2 0.13 0.03 0.05
151 0.09 0.15 0
Heat input ,
k j / i n .
(kl /mm)
45 (1.8)
75 (3.0)
100 (3.9)
45 (1.8)
75 (3.0)
100 (3.9)
45 (1.8)
75 (3.0)
100 (3.9)
45 (1.8)
75 (3.0)
100 (3.9)
45 (1.8)
75 (3.0)
100 (3.9)
C o o l i n g t i m e
from 800 to 500 C,
seconds
10
25
45
10
25
45
10
25
45
10
25
45
10
25
45
f t - lb ( |) a t - 5 0 F ( -4 6 C)
W e l d M e l a l
HA Z
39 53)
29 39)
11 15)
46 62)
42 57)
29 39)
68 92)
34 46)
29 39)
60
81)
11 15)
36 49)
90 122)
70 95)
61 83)
44/851
58 79)
32 43)
27 37)
72 98)
45
61)
24 33)
53 72)
39 53)
31 42)
52 71)
43 58)
32 43)
21 28)
32 43)
21 28)
120/0091
86 110)
84 114)
43 58)
74 100)
88
119)
26 35)
79 107)
77 104)
52 71)
83 113)
46 62)
73 99)
45 61)
29 39)
51 69)
TB/121
148 (201)
10 (14)
27 (37)
81
(110)
63 (85)
91 (123)
151 (205)
77 (104)
79 (107)
108 (146)
44 (60)
59 (80)
147 (199)
68 (92)
40 (54)
&
y xA°>
r-.yiysp*
•:.-Ah.^w-:><,
Fig. 14—HAZ structures of steel 231 (0.14 C,
0.06 Ch, 0 V) welded at different heat
inputs: A-45 kj/in. (68 It-lb at -50 F);
B-100 kj/in. (29 ft-lb at -50 F). Nital etch,
X250 (reduced 33 on reproduction)
C o n c l u s i o n s
A s t u d y
e m p l o y i n g
m e c h a n i c a l t e st
i n g a n d m e t a l l o g r a p h y a s w e l l as st a t is
t ic a l a n a ly s is p r o d u c e d t h e f o l l o w i n g
f i n d i n g s a b o u t t h e e f f e c t s o f c o l u m
b i u m a n d v a n a d i u m o n t h e w e l d a b i l i t y
o f H S L A s te e l s w i t h c a r b o n c o n t e n t s
r a n g i n g f r o m 0 . 0 8 t o 0 . 1 8 % :
1 .
Base Metal. F or t h e c o n t r o l - r o l l e d
s t e e l s o f t h i s s t u d y , t e n s i l e s t r e n g t h
i n c r e a s e d w i t h i n c r e a s i n g c a r b o n a n d
v a n a d i u m . Y i e l d s t r e n g t h i n c r e a s e d
w i t h v a n a d i u m , b u t w a s n o t a f f e c t e d
b y t h e c a r b o n v a r i a t i o n . B o t h y i e l d a n d
t e n s il e s t r e n g t h i n c re a s e d w i t h c o l u m
b i u m u p t o a b o u t 0 . 05 % . T o u g h n e s s
i n c re a s e d w i t h c o l u m b i u m u p t o
a b o u t 0 . 0 6% a n d d e c r e a s e d w i t h
c a r b o n .
2.
Heat-Affected Zone.
C o m p a r e d
w i t h C - M n c o m p o s i t io n s , c o l u m b i u m
w i t h o u t v a n a d i u m i n c re a s e d t h e
t o u g h n e s s w h e n c a r b o n w a s l o w a n d
d e c r e a s e d it w h e n c a r b o n w a s h i g h .
V a n a d i u m b y i ts e l f h a d l i t t l e e f f e c t o n
t o u g h n e s s w h e n c a r b o n w a s l o w b u t
i m p r o v e d i t a s t h e c a r b o n w a s
i n c r e a s e d . F or a n y g i v e n c a r b o n l e v e l ,
t o u g h n e s s w a s l o w e s t w h e n h i g h
c o l u m b i u m a n d h i g h v a n a d i u m w e r e
c o m b i n e d . T o u g h n e s s d e c r e a s e d w i t h
i n c r e a s i n g c a r b o n a n d w i t h d e c r e a s i n g
c o o l i n g r a t e .
3 .
Weld-Metal Toughness.
W e l d -
m e t a l t o u g h n e s s d e c r e a s e d w i t h d e
c r e a s i n g w e l d c o o l i n g r a t e .
For a l l 0 .08% C s tee ls , a 0 .03%
T i - B - 0 . 2 5 % M o e l e c t r o d e w i t h a b a si c
f l u x g a v e t h e b e s t w e l d
m e t a l
t o u g h -
yyy'yy
-
yy.'-yyytAyAA
Fig.
15—Weld-metal
structures of steel 151
(0.09 C, 0.15 Cb, 0 V) welded with
TB/121 at different heat inputs: A-45 kj/in.
(147 ft-lb at -50 F); B-100 kjlin. (40 ft-lb at
-50 F). Nital etch, X500 (reduced 33 on
reproduction)
n e ss . H o w e v e r , t h is c o m b i n a t i o n w a s
n o t e f f e c t i v e f o r
Ihe
h i g h e r - c a r b o n
s t e e l s t e s t e d u n l e s s t h e r e w e r e
s i g n i f i -
186-s I JUNE 1979
8/10/2019 Effect of Columbium and Vanadium on the Weldability of HSLA Steels
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a m o u n t s o f t h e m i c r o a l l o y i n g
m e n t s i n t h e b a s e m e t a l .
o o t h e r c o n s u m a b l e c o m b i n a
s g a v e t o u g h n e s s e s g r e a t e r t h a n 2 0
| ) a t - 5 0 F ( - 4 6 C ) i n a l l
Acknowledgments
f o r h i s h e l p w i t h t h e e x p e r i m e n
p o r t i o n o f t h is p r o g r a m . T h e e d i t o
c o m m e n t s o f B . S. M i k o f s k y a r e
g r e a t l y a p p r e c i a t e d , a s is t h e c r i t i c a l
r e v i e w o f C . F . M e i t z n e r .
References
1.
Box, G. E. P. , and Behnken, D. W.,
Some New Three Leve l Des igns fo r t he
S t udy o f Q uan t i t a t i v e V a r i ab l es , Techno-
metrics 2 (1960), pp. 455-475.
2. Hart , Peter H. M. , et al., T h e W e l d
ab i l i t y o f M i c roa l l oy ed S t ee l s ,
Microalloy
ing 75 Proceedings,
Un i on Ca rb i de , 1977 ,
pp . 540-551.
3. Cana d ian Cent re fo r M in era l and Ener
g y T ec hn o l og y , S em i na r H A Z T o ug hnes s
o f W e l d e d l o i n t s i n M i c r o a l l o y S t e e l , O t t a
w a ,
N ove mb er 16, 1978.
4.
Gar land, | . G. , and K i rkwood, P . R. ,
T o w a r d I m p r o v e d S u b m e r g e d A r c W e l d
M e t a l ,
Metal Construction
7(5) , Ma y 1975,
pp. 275-283 and 7(6), June 1975, pp. 320-
330.
5. Lev in e, E. , and H i l l , D. C , A Rev iew o f
the S t ruc ture and Proper t ies o f Welds in
C o l u m b i u m o r V a n a d i u m C o n t a i n i n g H i g h
S t reng t h Low- A l l oy S t ee l s , WRC B u l l e t i n
No. 213, February 1976.
(Continued from page 178-s)
E. B E TZ A N D H . K . LE U N G
v a r y n e a r l y l i n e a r l y w i t h t h e
o f h y d r o g e n i n p u t , b u t t h e
s i o n r a te is q u i t e u n r e s p o n s i v e t o
T h e e f f e c t o f p r e h e a t i n g o n
d i f f u
a l s o b e e n i n v e s t i g a t e d . T h e
h a v e i n d i c a t e d t h a t h i g h e r
t e m p e r a t u r e , e s p e c i a l l y a b o v e
C (4 4 6 F ) , w o u l d a c c e l e r a t e t h e
r o g e n d i f f u s i o n r a t e , a n d i n c o n s e
n c e , t h e m a x i m u m v a lu e s w o u l d
e d a n d a m o r e e v e n d i s t r i b u
s o b t a i n e d .
A n o t h e r a s p e c t is t h e p o s s i b i l i t y t h a t
r o s t a t i c p r e s s u r e g e n e r a t e d b y t h e
d r o g e n a l o n e c o u l d i n i t i a t e a t e a r.
u n l i k e l y . A l l e n - B o o t h et a / . '
3
e s t t h a t , f o r t h i s t y p e o f f a i l u r e t o
r , t h e h y d r o s t a t i c p re s s u r e w o u l d
e d t o b e o f t h e s a m e o r d e r as t h e
t h i s c a s e is e q u i v a l e n t t o a h y d r o
p r e s s u r e c a n o n l y b e a c h i e v e d
g h a n e x c e p t i o n a l l y h i g h h y d r o
n i n p u t o f 4 0 c c / 1 0 0 d e p . m e t a l
t h e r w i t h a n e x tr a l o w f r a c t i o n a l
i d v o l u m e o f 0 .0 2 % . T h e p r o b a b i l i t y
c o m b i n a t i o n o f r a r e e v e n t s is
l o w . T h i s i m p l i e s t h a t h y d r o s t a t
I n r e g a r d t o t h e c o n t r i b u t i o n o f
g e n to t h r o u g h - t h i c k n e s s d u c t i l i
D L „
r e f e r e n c e is m a d e t o t h e
- s t a g e p o s s i b i l i t y t e a r i n g p r o c e s s .
t s s h o w t h a t h y d r o g e n c o n t r i b
f a i l u r e as s u b s t a n t i a l h y d r o g e n
n t e n t h a s n o t y e t d i f f u s e d t o t h e
s u s c e p t i b l e r e g i o n . B u t a t t h e l a t e r
s t a g e f a i l u r e p o s s i b i l i t y , it is f o u n d t h a t
t h e f o l l o w i n g t h r e e f a c t o r s b e c o m e
r e l e v a n t , n a m e l y , t h r o u g h - t h i c k n e s s
d u c t i l i t y , b o u n d a r y r e s t r a in t s , a n d h y
d r o g e n e m b r i t t l e m e n t , w h i c h b e a r
e q u a l r e s p o n s i b i l i t i e s i n t h e l o s s o f
d u c t i l i t y . F r o m t h i s a n a l y s i s , it is
c o n c l u d e d t h a t h y d r o g e n c a n o n l y
p l a y a s u p p o r t i n g r o l e i n la m e l l a r t e a r
i n g .
C o n c l u s i o n
A m a t h e m a t i c a l m o d e l is g i v e n
w h i c h e n a b l e s t h e i n t e r a c t i o n b e
t w e e n te m p e r a t u r e , h y d r o g e n d i f f u
s i o n a n d s t r e s s - s t r a i n l e v e l s t o b e
s t u d
i e d q u a n t i t a t i v e l y , f o r t y p i c a l w e l d e d -
j o i n t s , w h e n t h e jo i n t is b e i n g w e l d e d .
T h r o u g h v a r y i n g t h e r e l a t e d p a r a m e
t e r s ,
t h e s i g n i f i c a n c e o f h y d r o g e n h a s
b e e n r e v e a l e d i n t h e c r a c k i n g p r o c e s s
o f l a m e l l a r t e a r i n g , a n d i t w a s s h o w n
t h a t t h e h y d r o g e n e f f e c t , i n t h e f o r m
o f h y d r o s t a t i c p r e s s u r e o r d u c t i l i t y
l o s s , c a n n o t o n i t s o w n i n i t i a t e a t e a r .
T h u s it is c o n c l u d e d t h a t , i n l a m e l l a r
t e a r i n g , h y d r o g e n is n o t t h e p r i m e
f a c t o r c a u s i n g f a i l u r e , b u t p l a y s a
s u p p o r t i n g r o l e o n l y .
References
1.
Kuma r , Ra jend ra , Phys ica l Me ta l lu rgy
of I ron and S tee l , As ia Pub l i sh in g H ouse ,
1968.
2.
Ha l l ,
E.O. , Yield Point Phenomena in
Metals and Alloys, M a c M i l l an Co L t d . ,
1970.
3 . S t. l oh n , C , and G e rbe r i c h , W . W. ,
T he E f f ec t o f Load i ng M o de o f Hy d ro g en
E m b r i t t l e m e n t , Metallurgical Transactions,
4, Feb. 1973, p. 589-594.
4.
W a t a n a b e , M . , T h e Pull-Out T y pe
Fracture in Ro l led Steel P lates , Proc. of a
S y m pos i um on We l d i ng i n S h i p B u i l d i ng ,
Lon do n, 30 th Oc t . t o 3rd No v . 1961, The
Weld ing Ins t i t u te , 1962, pp . 219-225.
5 . He wi t t , ) ., Hy dro gen in S tee l , ISI
Spec ia l Repor t 73 , London, 1962, p . 83-89.
6 . N ic ho l l s , D.M . , An Inves t iga t ion o f
Lamel la r Tea r ing , D.A .E . Thes is , Cra nf ie ld
Ins t i t u te o f Tec hno logy , Sept . 1966, 121
PP-
7. Bel le n, A. , Spa nraf t , | . and va n d er
Veen , J .H., S om e S tee lmake rs ' Exper ience
on Improv ing the Res is tance o f S tee l P la te
to Lamel la r Tear ing , II W D o c .
IX-778-72,
1972, 9 pp.
8 . N ish io , Y ., Ya ma mo to, Y ., Ka j im oto , K .
and Hi roza ne, T ., O n the Lamel la r Tear ing
i n M u l t i r u n F il le t We l ds , M i t s ub i s h i Heav y
Indus t r ies Te chn ica l R ev iew, 9 , (3 ) , 1972,
pp. 19-27.
9 . Oc h ia i , S., Yosh ina ga, S ., and K iku ta , Y .
Format ion o f S t ress
(Strain)—Induced
Dif
f u s i on o f Hy d rog en and i ts S o l u t i on by
C o m p u t e r - A i d e d F in i te E l e m e n t M e t h o d ,
Trans, japan Iron and Steel Institute, 15,
1975, pp. 503-507.
10. A l l en -B oo th , D.M . , and He w i t t , ) ., A
M a t hem a t i c a l M ode l Des c r i b i ng t he E f f ec t s
o f M i c ro - V o i ds upon t he D i f f us i on o f
Hy d rog en i n
Iron
and S t ee l , Acta Metallur-
gica, 22, Feb. 1974, pp. 171-175.
11 . K a u z m a n n , W . , Thermal Properties of
Matter, V o l u m e I—Kinetic Theory o f Gases ,
W . A . B e n j a m i n , Inc. , New York , 1966, p .
74.
12 . A l l e n - B o o t h , D . M . , A t k i n s o n , C , a n d
Bi lby , B .A ., A Nu me r ica l So lu t io n o f t he
D i f f us i on E qua t i on Res u l t i ng f r om t he V o i d
T heo ry o f t he T rapp i ng o f Hy d rog en i n I r on
and S tee l , Ac ta
Metallurgica, 23,
M a rc h
1975, pp. 371-376.
W E L D I N G R E S E A R C H S U P P L E M E N T I
1 8 7 - s
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Now Avai lable . . .
WRC Bulletin 246
February 1979
Interpretive Report on Dynam ic Analysis of Pressure Com ponents
This interpret ive repor t has been prepared by the Pressure Vessel Research Commit tee, Subcommit tee on
Dynamic Ana lys is o f Pressure Components .
The intent in wr i t ing th is repor t was to summar ize, in one document , a br ief background descr ipt ion of areas of
concern to t he Subcommi t tee as we l l as in fo rmat ion cur ren t ly ava i lab le t o indus t r y and to ass is t in de te rm in ing
the course of research th is Subcommit tee wi l l under take in the future.
The Subcommi t tee in deve lop ing th is repor t has assoc ia ted the cur ren t t op ics w i th t he Subcommi t tee Task
Group assignments. Each topic has been wr i t ten so that i t can be read in i ts ent i rety wi thout having cross
references to other topics. This was done for c lar i ty and to develop a procedure for inc lus ion of future work of the
Pressure Vesse l Research Commi t tee . Subcommi t tee on Dynamic Ana lys is o f Pressure Components .
Publ icat ion of th is bul let in was sponsored by the Pressure Vessel Research Commit tee of the Welding Research
Counci l .
The pr ice of WRC Bul let in 246 is $10.00 per copy. Orders should be sent wi th payment to the Welding Research
Cou nci l , 345 East 47 th St . , New York, NY 100 17.
A l s o
R e c e n t . .
Weldability of Steels
Third Edition
by the Welding Research Council
The th ird edi t ion of the book Weldability of Steels was pub l ished to update t he in fo rmat ion and make the book
avai lable again.
Specia l credi t is g iven to Messrs. C. W. Ot t and D. J . Snyder of the
U.
S. Steel Corporat ion for updat ing the
appe ndix tha t con tains the table Steel Co mp osi t ion s with Suggested Pract ices General ly Required for Sound
We ld ing and the Index o f S tee ls in t he Weldab i l i t y Tab le . Th is in fo rma t ion shou ld be o f va lue to a l l eng ineers
concerned wi th we ld ing .
The pr ice of th is book is $18.00. Orders should be sent wi th payment to the Welding Research Counci l , 345
East 47th St . , New York, NY
10017.
WRC
Bulletin 242
October 1978
Fatigue Behavior of 5 0 0 0 Series Aluminum Alloy Weldm ents in Marine
Environm ent
by W. W. Sanders, Jr. and K. A. McDowell
The repor t represen ts t he resu l t s o f a s tudy o f t he fa t igue behav io r o f 5000 ser ies a lum inum a l loy we ldments
submerged in seawater . Tes ts were conduc ted on p la in p la te , t r ansverse bu t t -we lded and long i t ud ina l bu t t -we lded
spec imens o f 5086-H116, 5456-H11G and 5456-H117 a lum inum a l loys .
Sup plem ental tests were cond ucte d, inc lud ing fat ig ue tests of s ix p la in p late spe cimen s of ABS Class C Steel .
Studies a lso inc lude the measurement of weld angles at the point of crack in i t ia t ion in welded specimens, f in i te
element analys is of a typical but t -welded shape, d is t r ibut ion of res idual s t resses and weld qual i ty evaluat ion.
Pub l ica t ion o f t h is bu l le t in was sponsored by the A luminum Al loys Commi t tee o f t he Weld ing Research
Counci l .
The pr ice of WRC Bul let in 242 is $7.00 per copy. Orders should be sent wi th payment to the Welding Research
Counc i l .
345 Eas t 47 th St . , Room 8 0 1 , New York , NY 10017 .
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