SCIENTIFIC ABSTRACT LASHKO, N.F. - LASHKO, N.F.

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• Collection: Scientific Abstracts
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• Document Page Count: 100
• Document Creation Date: November 2, 2016
• Document Release Date: June 20, 2000
• Sequence Number: 20
• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTRACT

_i_~61icl -Sit _~olutlon of -do-
foFtned tkustenite.
M., 41,164, J,;ISHKO ;IMM
I I'munr IM-11. Nank' .3cr. ra.
15, 76-90 0,-A steel of the C 0.47, Ni 15
;7.ed far 5 firs. nt
Cr 13.5, Sl 0,5, find hfof).3%was=1
l2rA* avid queliched, with 1110, Afelitilographic examn,
by tile method of oxide fornintioti on samples, deforliml by
pressitres tip to 300 kg./.qq. mirt, show that lite decompit. of
atistenife is famer thati on nolidefortsird sample%, Tr ) I I
Ir Itil
carbides gradwilly are Iraniformed inin cubir earbiffes.
The time of appearance of ctjl)ic Carbides k Pivell fly tile
%vhcrc Q - 47,7M (-.0.1degiev for
iinstrained, 75,11M for strained lattices. 'Ott agchir Me -t-
phase loses Cr which leads to a srpti. of the -r-pbav%into.
layersand tile tviyearance ofa new line in lite x-ray ifingram
corresponding t0:% chayiged parmic I c-r off lie -Y-plla-c,
S. Pak!;iver
I
v
a_
Unt
it ~7,
wr3.W?

CZ
CA
Woct of incre"Im the strut"d Tbeosity 00 the Proem
a7staluxtum of blowy oabKuu in S. V.
vskyan and N. F. lashko Z.'--. Jrss. Whux. 23.
49D-2( 1951).-As study of an factors
fiecting the crysta. of binary tutectics (C.A. 43. 1000s).
tb
=
a., was udcr~y of addirtir 0.1.5
~4
I a( atLr-%W to the aptcou KCj-XjCr#Oj-HtO and
InkOU&jNOt-jljQ w as to fupprm convection and cone".
gradients. M adda. faran dendritk growth of one of the
eutectic phases but does M change the character of the
crptts. proctsa, In this respect, the suppression of con-
rectiou and cc=. gradients acts differently frm the in-
crew of und-co".. Michel Boudart

qd9dits in hmary qd..
S. V. Avakran and N. F. L.,hko~ Zh _
10"10950-A vAc-r-c-aco*--l , lw' Fill. Kimm. 23,
00 XX0s-NaN&-a`i-d- Of the systeni;
~-HA Akii-an. As-C,-
ai-im-as Is.& to the conchwou thAl
krimoom of Unary tutoctk lituetur"
10 orwy welvas is My dwiar to
forroation in 1144 P"Mi" rultok
mum symems. BP8CW feature$ am due to
ths faet that In tammy sys"I'l- mtmk crIsta. takes PLUX
wid" a gi-- F.W. of imp. -W C0nCn. . During Cryan.
the compa. ot am liquM chamm and approct,., tj,. Co.
a, the ternary "fiectic. N ought Pa.
vekxity at Cryan. to affe" am Ifimr-
mm Veen" at the, ON the bimairy eutectic (T,,. ),
no. of Imi" of the b t" COMPOutnt Ought to docreaft the
inary cutectk. wn" Cryst, takes place
'a a IUM IP In a teromy
W bmodW =tIall by "-- tbc VUW abould
y mrm Instead of by Plant
*urlsm, &'Dc' th's Ulb'd COCOPOSect decresm tM
of.cryst..6roirth, 'UPY
Ukhel K=Ul

IASHKOI N. F.
USSR/Chemistry - Metallurgy 21 Nov 51
"A New Intermetallie Compound in the Binary System
Fe - Mo," R. P. Zaletayeva) N. F. Lasbko, M. D.
Nesterova, S. A. Yuganova
"Dok Ak Nauk SSSR" Vol LXXXI, No 3, PP 415, 416
The similarity between wolfram and molybdenum led
the authors to believe that a compd analogous to
Fe2W should exist. They were successful in finding
I'the new phase Fe2 - Mo in chromium-nickel-molybdenem
austenIte steels contg a small amt of carbon.
2ATl6

t7 nnn

1n-.Uua*:r6-t], An* wutX 2, 4; ind -7 S4 lxrro
RR J'arnace'and ouL 7m .1% Y VAB
ibo A3-M~40" - Alloy Ras &Ft~P%uw, bla
1
1W
a,
,0
al
on axim
iq 4%, 1V00
1 The
4
1. Il
had two phasca up to the ell a
I ;
Ut-Della allactu". MOM
"M
f U-
ite
d
d
n
i ~kw b
whit
en
r
s o
cou
a
0moge
y. a
m-ond phut~,
CW W C,
l
i
la
l
b
h
de
il
i
1
6
t
causei
n t
o
a
Bo
. irit
n
l
wir amw
k4, So
a
Pat
t
lilm~.Untl thb,waoulit a 010 woma Plub decreased
si - af4ply 4t-ljw(L MeU4 UP-4 04 Mole,
jux. !Atibility of S1 in M is thus The otsound phw
bo Waloa by anoffia aching, -riy im ga
-ged tha it bri t, fato--contmd 11164 or thb sul*)iattlu).

L
xat all Anneal
tjTo (CuiM),
Ing' tcillZ - The data Indicata tbat the ak-owl AM is Ni.,Bi
Its superUttim parials, rikht up to th -a melting ".~ axA.
i
~asu?ftl
hav's
wM X31
W
t
d
it
A
t
T=e*4
t
c
us
61
.
t
r6M%M
,
a temp.). TaAt of tbe, Swid Man, is - 2;2M W intro-;
-ta
dum'ng Cr, W6M Is -M cod by. Xi,(SjA)

IASHKO, F.
LISO/Engineering Welding Jan 52
ItConcerning the Weldability of Metals," S.V.
Avakyan, N.F. Lashkol, Candidates Tech Sai
."Avtogen Delo" No 1, pp 29-32
Discusses definition of metals, weldability and
outlines conditions required for realization of
welding process which is considered as interatomic
cohesion by diffusion. Analyzes welding process
discussing crystn of welded joint and changes in
properties of-,base metal under effect of welding
heat. Shows microstructure of Bi welded with ad-
mixt of Cd and Sn in'3 micrographs and discusses
welding of unlike metals
212T18

USSR/Metallurgy - Welding, Crystal~' Jul 52
C%'N lization
r-T.
CIN
(n "On Discontinuous Crystallization in the Welditg
Process," S.V. Avakyan, N.F. Lashko, Candidates
Tech Sci
"Avtogen Delo" No 7, pp 25-28
briefly reviews Soviet tech literature on sub-
'Ject and disputes periodicity of crystn in
VeMed joints accepted as an established factor
by some investigators. Concludes that discon-
timulty of crystn during welding is conditioned
by (1) balance between heat delivered to boundax7
233T43
of solid and liquicL phases and (2) heat loss.
Substantiates this assumption by crystn of salol
under conditions similar to those of welding.
233T43

7

~h is for
F. series of a i
d srAuli~&
_
1k
M
find
-
.,
QUM.
flio kij
~M
uUm~V4MjI
.
4
5-w9 Ref
~
ckb
;
I
Aui! Fix, 1954. Abstr, Nu.

ed tht cmdidoa for:the forma" of meta-
t about
b
h
e
ti
f diff
h
di
l
W
t. t
ar
o
e3 on prm-
lestzt t
at d
e
nsac
us
~td
- rnade oil the let
m~ Ttex-my pham zrW)si9
n
'5~ 16 the anode soln
,Df 3 Cr-Nisterl at contala Ti
X
.
be-7-Fly
;or Zr C~ and "-AT"--T
the Ti steel exhlbl~ 2 systens oa lium that correspond to TI
E,3,: 'de.
zapblde and Ti tdtr. -The paf&mzct~rx, for. thek 6inpd
these substnucts in I
art cloot t6 the values for
'
Dine&fU
tep3.m
-Wtu fact
_*t
-
,
St4tt f
rustouttnuous
the esrbldes =d t6trwes i~
the equil
us

d solils
i;~_In abiv6i the non-
equH ryna bides andultridesL-1 Ozisolidificat=*

of Cr-m Stre, 61
'Rovt L
ar
eb from r~ ts
J
.
.

1 7~r

teTrRnsfor=t1m of carNdic and csxbWftM).- -pba-sei Im
tbdaflu LpAkd; W. D.

4 -3
J*U

0
=
R
IID-17, JW&raj. ZA
'
)
]V'
Xhi
T
-
,.43
m 1054
o
7
43
1
u=e-cmaim a3 affected
bY N E=tent i3 'TIVO StCd of the El M type
1
mntg. 0.3 and 0.10
% N were studied, . Both hardened and
*
anzeoed spc6mens wen ilivewriltdi- the
bardezanx was
'
irom 120D
in water. the Atnul fa&s) was ja OM.~'.
Zl
k
il
ectrWyt
ay obl
zed pptj~ I-*= both steds. were ams.
~ ra
bk
Tl
th
b
d
b
d I
OFTI
&
n
e pow
er nitt
o
1
y,
y
nqmTp
diam t
camer" o! 57 mm
on
pe of the
.
studitd pbase
eno
TOntr
rRM2 were obtained wi Fe
Cr
1

-4" ,
6
.
,
9
adn. the cubiml i:arbW Mr.lZostpd. -out with
v predazliant c=ttnt of Cr and the double FeWo mbide
*
14 Ohm x Is 2 or 3) hming
a pammetti of 10.04-
11M A. dtpem4ng on the wndItionsof 4ul.: seng
Bo~l arhMai spr4" By lnaiki4 t1hi 0
d=t1m and utnp.,bf tizing

;rw
-tf
drttatd ront
eno
kall
s
h a
amm
r Ej tL
c_
L _
y.
t p
: ~r
I
l
p
W
bid-
t
t
d
l
I
i
n
=
.
uce
navase
cm
a
th I
ang dumtiaa of
w
=
isothaml 2-shig and witb Inansing tmp. of-iring. In
the st&J, cont
0
18 !q ibt cubld
hRse combied onl
.
s.
m P
y
*1 tb-.dDuble =bovitrija -M
M:(C;N) bming a CrIst
.
.
'
_jatke with a paT=b1cr of 1US-10M A
7%e
ammeter

7
j. .
.
p
b
d
1
etryst. lattk~olthado:iblecarb6DftrkL-in=ti~ed With
'
d t3on
Mcfeming UM of S&S. ~ In 4 Steel 4 the MY M5 type
05
t
0
ud
b
N
e
ti
-
con
-
i
L
e oth
t.
r 'Onnicru in.the same quan
%
,
4
tim as the tw
t~6501
M=
u
n
i
d
0
ii
P.
. o
a
a&
nj a
p0
; sep
carbonitride
'emetic 10
% A
.
.
_
cbrm. snaly.,Os of U
3 hceabop.1Wdt;MvfC.W $bDWedi N

N &Ad at n Ealing coxiftnt of it the doulyle ~irbmt bv=v

7
0
11
d
.1

.2 1~4 1 -~) /Y. /-
AVAKYAN, S.V.; POGODIN-AlEKSEYVI, G.I., doktor takhni-
-WUMRn "dsalrmo: professor, redak-tor; POPOVA, S.M., tekhnicheakiy
redaktor
[Metallograplq of welding; some problems] Hatallovedenis evarki;
nekotor7e voprony. Pod red. G.I.Pogodina-Alakeeeva. Moskva, Goo.
nauchno-takh.n. izd-vo mashinostroitallnoi lit-ry, 1954. 270 P.
. (Welding) (Metallograpby) (MLRA 8:4)

T-A
W M I)W- m :grain. -ray ~ra
'from sInklo. kra!6 sbaw, the developmint of a4te,Ls'
L11 up
Is 6Ompw)4*ltb ow fr4gmcntat~)I, ~ -
to -1% Amin. As' siminIncreabw the saterien13 bicon,
hpll intenw, and b pattern oF sharp spots dBvclopo, dio-o-mg
ally.&sanse, 1hporimessuered
"Ibed thnt the original grain Ism brokers up into a ILrge jiufj,b,~j oj,
al=et perfect cr):;ta%tc3 Wtb orientations scAtternd ov(-~.r
0,3 kg-Imm'3.
it bDO'; iC G6f & Oift Of. wigo of sov" dogmea. Experiments at hi
m=1nea by
I:A~Ivwidas stages in the Ust the specimen $-, dtformation ond o*xr temp. give Pimfiar qualitativu
brAk-Teflectior. IAjo pbologmpbs from The dimm6onsof fhv~ blacks, however,inere-amuith
i single grains. Up to -04% strain (1 hr.), deformation h by temp. of dalbrmat3on and decreaw with inererxiiflg q.,
id1pon one oratmost twoapsysteM& Inthsper!Ddl--2Dhr. drIormation. Ill-] Results on pure U are aurran-i p
~-I% strain)_ znwt grains sliow 2 or 3 aZp sizterna operatis,'. followE : meavery takm plave in creep by 0.,
hereafter the surfambecemes apFarently folded lund slip lin- graL" into blmk~ the boundaries of whiiji am elti1vt h)r7n,r
F~*Maoto 100hr. (-M%fitsb) the alip bands or ionner kinlai~ In either case wmc prw,- .,t
-an IntemBfing pattern dividing the
folds form fonnBr jv~in' diffusion i3 rsoocswy. Thus it iH intereiiting to Btu,!, O~z
-7n

;villwr moromIrm rrhijily than 1P pDrOintIft1s. "In imAkillar,
it iti iriteirsting,to AW vhnt brippena in supprasturatod solid
FAIL' ir'brzo IN-. diffusi YOMP.Ixg firr Wcom lartiDd by piltri.
Tho ago-hardenhigill'oZI! 11P
(4vasiawd. Thli
plift Mg.8i 1sinnil partiellr4), Al,Cu3lg, which is pre.
6" ~t afGr plastio deformnlion in tilt, form or rods, and
of . swidblotlo.
ged for 10 fir. at 1701 C. Exicinsive scriDs of experi-
Ynents wero carried out. (1) at 1210F C. uith a 8trcs5 ofj(),kzg.,~
irim's ^ It Mt
rim.2,
410riell the -Wnsionjilmo orri! wan llnj-~jr lip to ;10 1jr,, after
trcep lftri~ cleratt-il m;,r3,,vdly, At V& C, thrre werc no
-fisIble signs of dtfDrmntion up'to 40 hr. (-10' rxt,~wion),
/0
and. then alip lints aFF-51-111. Up to "M hr, (_5% extension)
I
deformat only by slip an I'Llotemp.
was too low forrhl-hic pptu. At 70 h-. fraLlurn o-mcun-ed by
wking~ in ihe wrk hardnms iras much rziducid, but in the
rest
of the ispecimen tho hardnevi -;i-as unchangM from thD
start.- At 3* C. thera-wrre no -visible Figns orej .ip, &T.., until
jitarly 40,rb,' 1 (-04% extgrislon), although tho ho-rdntm as
meattivred w' Jth a ball indenter had fallen >201;'~~ Therafttr
uji 0 -CO br. definrmation was by slip, -which dividtsd tho
Sha_
_d MgiC_n.
the boundaripz of
"WhI01 became sites for Selective Pptn. At CD-E0 hr. (0-7-
V nsion~a tr~- )CM ft~DT ip to blork deformation
look IN66's- tho R114
8.7, 1 1 - 4
1~yl jj)jr~etl by -flitin. Fnehiro ocrurrt-41 nt
rxtollition), by which time the hardness lint) fallvil It) (11-A hird
its iniiin) YAIYt it, thp rr,"ityn of nreking. in r!ihsidi;ir% r_x Tv.-ri
brol;c arter I hr. at 200' C. and 17 kg.lrnm
iris of thp regitlar block t)T,-,, tilthough thc
imdvT a atrm or 4 kro/nlrri-l tntentlud 20"; it, I C.
and 17 kg./mn. .1 bef6re brenking. In t1ills ra!~( dvfrqmllfic~a
vi-ne by iriiegular blwks, the boundaries b(!itir 1-a. k! y c,u!;jrrcd
by pr~rlpilatv. ]it geneml, riti-drig tho tump. (4 d ..... imr-tion
;jj)Pctletl up thp theingti froin slip tn Wkwit d0orin,own A!
Flifficirrith, W01 temp. thi, form of defw
init-, i
rclitioit of a Veriod of not-mril Mip. Conchisionz r,re The
"
absenco of enbrinced pptn. in the
shows tbatsur1deformation is not, &a has been Fualz~-t~-,l VISO
whrm.n diffusion process bnt invulvm shp tot) fine to he
resolrA ky the micmiscope. (2) Somo of flict-v fivi, gljp~; M-W
Mw to ` critical size ", which is flefined ni t ho sizo mich t hat
further slip *it that plane results in a decrea- of free ener;7y.
These slips then grow to be, T1.1bit- slip luic.A. 13) The
transition from cleformation by interftecting rv,tcrn~ of blip
linsa to block-fomittion requirc-9 diffilgion (it d!-! 1)"t,
opcuTindtformationat 200' C.). (4) Hinks an. not r, fvnturp
of deformation of the Al alloy.-A. F. B.

FD ~-363
USSR/Physics Alloys, Fatigue
Card 1/1
Author Lashko, N. F. and Radetskaya, E. M.
Title Fatigue processes of deterioration in alloys with "annealing twirric",
Periodical Zhur. tekh. fiz. 24, 417-424, Mar 195k
Abstract Discusses nature and formation of annealing twin crystals and their-
effect on fatigue failure of alloys. Studies behavior of steelDs
EI-437 and EI-395 in fatigue testing, concluding that not always and
not in all alloys annealing twins cause fatigue cracks. Nine refer-
ences; 8 USSR 1939-1953. Photomicrographs.
Institution
Submitted October 17, 1953

14. __ i N -
USSR/Metals Austenite residue
FD-577
Card 1/1 Pub. 153-17/28
Author Lashko, N. F.
Title Variations in concentration in residual austenite
Periodical Zhur. tekh. fiz. 24, 884-888, May 1954
Abstract Discusses the problem of the decomposition of austenite during the
cooling of steels. Describes his experiments on the determination of
the nature and composition of the so-called "residual austenite".
C-me to conclusions that contradict the "universally accepted" concept
of residual austenite, as held by A. A. Popov and V. D. Sadovskiy.
Institution :
Submitted : March 27, 1953

LASHIO-AVAKYAN, S.V., ka~idat tekhnichaskikh nauk; LASM, U.Y., kandidat
takhnicheakikh nauk; ORWYA, V.V., inzhener'.4~~-f-'Met-Xi-
Intercrystalline cracks in alumimm alloy weldings. Svar.proizv.
no.1:13-18 Ja 155. (MLRA 9:4)
(Alunint, alloys--Welding)

uti

1, 25a--tS---0nrnpn. a d =A. u! mrb3ar phi~~3
--I;d 6t~,-r ~'I) C.,
0.9 ard I'S", (2) Mo 0,24 azd 1.0, (3) V 0-33 a:~d 0-91~ (41)
1'i O-Z7 ar.3 O~W, : ar (5) Cr 0.6:.t and I.-e2 plw !-.Iv 0.!~5
0.807c, rcsp., whi.cb h7-db=i
"F EDO, afid 5W4 for ptriods tf~ to 2OW hrs. F7I~

-le -.rzd 5trm r-,WmU-.Tt were (1) s coaZu- lfir~n
h Occre -low b
w
-a- de phLsp ne ;I cu ci!
c zbid -, (2) high aljoy coa+Azt of st, bid R
vafia)Ac compa. --m- pptd. or. hcatiue, (3) bigh mloy
lit
,
-lil
ly d
l
t
f
bt I
i
f
d (4) th
p
s*
s
&a
o
s
, an
ermi
&c n
u
a
y o
v

. . . . . . . . . . . . . . . .
7
.
-
W
t- ~e

PERIODICAL ABSTRACTS
Sub.: USSR/Engineering AID 4183 - P
LASHKO-AVAKYAN S. V N. F 1AaH40, and V. V. ORLOVA.
MEZHKRISTALITN'i-M TfmftffYKT~~SVARNM SOYEDINENIYAKH IZ
ALYUMINEVYKH SPLAVOV (Inter-crystal Fissures in Welded Junctions
of Aluminum Alloys). Svarochnoye proizvodstvo, no. 1, Ja 1956:
13-18.
These authors present results of their research and the experiments
of other scientists on causes of crystallization and occurence of
fissures in w*elded Junctions of aluminum alloys. They describe two
devices for determination of the deformations occuring in metals
and alloys resistance to crystallization. Results obtained in these
delicate experimentations are anal sed and practical suggestions
made. Two sketches, 5 graphs and 9 microphotographs ("Fractographs").
7 Russian, 4 non-Russian references.

x
- LASHED, 11-7., kandidat tekhnicheskikh nauk; JAGUO-AVILKW, S.V.,
11 - tekbnicheskikh nauk.
SwmwuT of the conference on hot cracks in weldecl joints, cast-
ings mA Ingots. Liteproizv. no-10:30-31 0 156. (YTRA 9:11)
(Founding--Qolity control)

"eels ;U'r6ve 1w T
R. Flstonvv%, N. -As-
Ah-
I
Yguk S
Ss
'Mz:
.
.
'
.
Fizz. 20, `rT'-_'Te2= ia bardLess !z V, Mod
rk
and TlAtet~s=.ealcd
=153. ThiS p6mDanut-non is ==.Ily ItUTib-.Atd to carbide
formption. Two, sutzhod.4 of diffe=tW mrbidt
Anoysis
mn uzr4 in, thL paper, earbide rr-Adue wis
i Wtd in IRC4- Ois ilisi-Aved itmenOtc but Wt VC~XfchC.
-
l
l
1
nd
An n1c. ssaln. c! 1j
Lj% left c&-
IM undi5sd
ved. _(21
rarntite mid:_si~j d &~scjvcd VC, Mo~f_', tad &W TiC
It F f_-Its Rw-t ?.dlded. 7"1t. Inve-kilgat~ --It& contained
C Oa-o-S, 1V ;!'17101,3-0,5 nr Nfo 1.71~lp. fley
Ow. t~T"IOU".

0.51; citric scid- Tbtlaxgtstzmt.oIVCo,-)dTiCisfwr-td
at zn--eal tt=p3. whkb give seco--dary hadness (in MoIC
M
low-C content only). Cementite d
r isappcared if enough
V, Mo, or rl was prrsent to bilid an C. Metastable c'-
meathe is 2, mecessiry idZredlent Icer the devr1opment o1
scconilary hardness. VC =dM do noi contain ft. VC
can disolveup "--dness. An
x-ray investigation revealed a ejoagulation of cementite
at;pve -4w,.

IASHKO. Nikolay Yederpricb- Yerenin, Nikolay Ivanov!c1l; RAI-'Hz;hTADT, A.G..
WN i~ilkh nank. doteent, reteenzent; A.A.,
Innbener, redaktrr; SWTURINA, Ye.h., redsl~-t,,:- jzlrt,..3:lrtva;
6AIAZKOV, tel-~nicbeskly reaal-tor, M!TVi,7.-"V,'., Ye-N., tektniche-
skiy reclaktor
f
LPhase analysis sad structure of austenitic nteelnl Fazovvi analiz
i strukturs austenitRvkh stalei. Moskva, L4os.na-:.(,bno-te!7hn.i:~d-
vo mashlnostroit.lit-ry, 1957. 234 p. 10: 10)
(,teel)

137-58-2-3920
J.
Translation from: Referativnyy zhurnal, Metallurgiya, 1958, Nr 2, p 23\5(USSR)
A UTHOR: Lashko, N. F.
TITLE: Phase Transitions in Precipitation Processes in Alloys (Fazo-
vyye perekhody pri diffuzionnykh protsessakh v splavakh)
PERIODICAL: V sb. : Fiz. -khim. issled. austenitn. splavov. Moscow, h1ashgiz,
1957, pp 69-74
ABSTRACT: A number of variants of structural changes in alloys, which
occur when the alloys are transferred from one isothermic
medium to another, are examined. These changes occur in ac-
cordance with the pattern, where O~. a solid solu-
tion, changes in composition with time, A is a metastable
phase in a second medium, ande-is a phase in a stable equi-
librium with the solid solution. It is shown that for transition
processes from the (3 to the r phase the difference in the
bonds of the elements in the precipitating phase and in the
solid solution, and also the presence of a concentration grad-
ient of the elements, is of major significance. The major
shortcomings of the existing methods of analy5is of phase
Card 1/2 transformations, based on use of the Thomson equation., are

137-58-2-3920
Phase Transitions in Precipitation Processes in Alloys
analyzed. On the basis of the general conception of the critical size of
the nucleus, problems of growth of the metastable P phase are analyzed.
V.R.
1. Alloys--Phase transitions 2. AUoys-Preoipitation--Phase transitions
Card 2/2

L /Y~ 137-58-2-3939
Translation from: Referativnyy zhurnal, Metallurgiya, 1958, Nr 2, p 237 (USSR)
I
AUTHORS: Yeremin, N. I., Lashko, N. F., Lebedyanskaya, N. 1.
TITLE: Phase Transofrmations in Austenitic Steels During Plastic
Deformation (Fazovyye prevrashcheniya v austenitnykh
stalyakh, proizkhodyashchi)re pri plasticheskoy deformatsii)
PERIODICAL: V sb.. Fiz. -khim. issled.. austenit. splavov. Moscow,
Mashgiz, 1957, pp 91-106
ABSTRACT: Magnetic microanalysis was employed to investigate phase
transformation occurring during cold plastic deformation in
the following austenitic steels: E1505, lKhl9N9T, E1434,
4Kh74Nl4V2M, 19-9, EM405, E1407,Khl8NIlB, 16-33-3.
E1388. It is shown that softening occurring on deformation
facilitates the r6-b-Ce. transition. Phase stresses are partic-
ularly great in the case of precipitation of the CY2
. phase
along the boundaries of highly deformed grains. The process
of slip is accompanied by lattice distortion, and shear stress
results in viscous slip along the grain boundaries. Decompo-
sition of 1~-with formation of Of
'g on the grain boundaries occurs
Ca rd 1/2 only in instances of slow deformation. In the event of signifi-

137-58-2-3939
Phase Transformations in Austenitic Steels During Plastic (cont. )
cant deformation, the r-01 transition appears along the boundaries of
. . 2.
twins. The rate of transition increases rapidly as temperature drops,
and precipitation of the 0(2 phase results in hardening. The r-i_oe,
"%s
transition is reversible. The temperature interval of reversible tra -
ition is below the temperature of crystallization. Ni, Cr, Mn, Mo, and C
stim*ulate formation of an O(p phas.e to different degrees. The solid rsolu-
tion becomes less stable on precipitation of a carbide phase (Me, Cr)23C6
during aging. Metallographic and x-ray analysis of structure yielded
concordant-results.
Bibliography: JB references.
V.R.
1. Auatenitic stools-Phase transitions-Effects of deformation 2. lus-
tenitic steels-Zeformation 3. Austenitio steels-Phase transitions-Mag-
netic analysis
Card 2/2

J f
137-58-3-6251
Translation from: Referativnyy zhurnal, Metallurgiya, 1958, Nr 3, p 259 (USSR)
AUTHOR: Lashko, N. F.
TITLE: The Effect of Manganese and Nickel Contained in Some Austenite
Steels on Their Phase Composition (Vliyaniye margantsa i nikelya
v nekotorykh austenitnykh stalyakh na ikh fazovyy sostav)
PERIODICAL: V sb.: Fiz.-khim. issled. austenitn. splavov. Moscow, Mashgiz,
1957, pp 126-130
ABSTRACT~ When Ni enters the crystalline structure of Fe, it increases
the parameter of the NFe lattice and reduces that of the rFe
lattice. The effect of Ni on the phase composition of alloys con-
taining 0. 2 percent C, 20 percent Cr; 2 percent Mo, and 1 per-
cent W was studied by means of experimental melts containinv
10t 20, 40, and 70 percent of Ni. Ingots thus obtained were forged
into rods from which experimental specimens were made - These
specimens were tempered in accordance with the following two pro-
cedures: 1) heating to 11500C, followed by two fours of cooling in
oil and 50 hours of aging at a temperature of 8000 ; 2) heating to
11800 followed by two hours of cooling in water and 200 hours of
Card 1/2 aging at 8000 - An electrolyte containing 300 g /I KC1, 50 c, /I

137-58-3-6-151
The Effect of Manganese and Nickel Contained in Some Austenite Steels (c Ont.
sodium citrate, and 50 cc of concentrated HCI, was employed in a Process Of
anodic dissolution at a D of I amp/cmz . Precipitates obtained after the
anodic dissolution of metal exhibited a comparatively homogeneous chemical
composition. According to data from x-ray analysis of alloys containing 10. 8
percent, 21 percent, and 39.0 percent of Ni, these precipitates are composed
of cubic carbide of the type Me 23C6' The precipitates of the alloy containing
72.7 percent Ni consist of trigonal carbide of the Me7C 3 type. The effect of
the variable Mn content on the pha:,e composition of Cr-Ni steel of type 20-20
was established with the aid of three experimental smeltings. The Mn in the
anodic deposits appears only in the carbide phase of the Me 23C6 type. Conse-
quently, as a carbide -forming element, the Mn is more active than Ni. In-
vestigations have also shown that Cr is a considerably more active carbide-
forming agent than Mn.
V.N.
Card 2 /2

~, I , 137-58-2-3942
S A-
Translation from: Referativnyy zhurnal, Metallurgiya, 1958, Nr 2, p 238 (USSR)
AUTHORS: Yeremin, N.:[., Lashko, N. F.
TITLE: Or. the Distribution of Nitrogen Between Solid Solution and
Second Phases in Austenitic Steels (0 raspredelenii azota
mezhdu tverdym rastvorom i vtorymi fazami v austenit-
nykh stalyakh)
PERIODICAL: V sb.: Fiz. -khim. issled. austenitn. splavov. Moscow,
Mashgiz, 1957, pp 131-136
ABSTRACT: The effect of N on the stabilization of austenite and the
distribution of N between the solid solution and the precipi-
tation phases in E1572 steel was investigated, wherein the N
concentration attained 0. 26%. To distinguish the effect of N
on the suppression of an 0( phase of various types, a melt
with a higher Cr concentration, facilitating formation of 8
ferrite even at high N content (0. 165%), was smelted. The
specimens were subjected to a special form of heat treatment
(Prosvirin, V.I., Saverina,I.A. V sb.: Voprosy metallove-
deniya austenitnykh staley. Moscow, Mashgiz, 1952). A pre-
Card 1/2 cipitate was obtained by electrochemical separation of the

137-58-2-3942
On the Distribution of Nitrogen (cont.
phases. The carbide phase~'"M~23C was separated from the carbide and
carbonitride phases MeC and MeW and the 0( phase by boiling in HC1.
The precipitate was subjected to x-ray and microstructural analysis. N?
introduced into E1572 steel remains in solid solution for the most part.
Grade 19-9 steel tends to formation of 6 ferrite yielding a Cr phase on
aging, when it contains ferrite formers. The presence of N2 eliminates
ferrite and the formation of a metastable 6phase arising on plastic
deformation.
:L, steel-Transfo=ELtions-Nitrogen distribution
_Zffects of Nitrogen
V.R.
2. Austenite-Stabilization
Card 2/2

137-58-2-3943
translation from: Referativnyy zhurnal, Metallurgiya, 1958, Nr 2, p 238 (USSR)
AUTHORS: Yeremin, N.N., Lashko, N.F., Lebedyanskaya, N.I.
TITLE: Phase Transformations in E1572 Steel During Forging (Fazo-
vyye izmeneniya v stali E1572 pri kovke)
PERIODICAL: V sb.: Fiz. -khim. issled. austenit. splavov. Moscow,
Mashgiz, 1957, pp 137-159
ABSTRACT: The changes in the phase compositi6n of E1572 austenitic
steel (19% Cr, 9% Ni, 0. 26-0. 36% C) were investigated with
the object of determining optimum conditions for heating and
cooling after forging. The processes of formation and change
in S ferrite, ferrite in the vicinity of the carbide phase, and
ferrite arising as a result of plastic deformation, were also
studied. Separation of the carbide phases was performed by
making use of the selective solubility of carbides of the
M023C6 type in hot HCI. The type of carbide was determined
by x-ray structural analysis. Ferromagnetic phases were
identified by magnetic analysis of the microstructure. It was
shown that 6 ferrite develops as a result of nonhomogeneous
Card 1/2 dendritic crystallization; its amount may be reduced by homo-

137-58-2-3943
Phase Transformations in EI572 Steel During Forging
genation at 12500. To avoid formation of 9 ferrite, the final stage of
heating and forging of the bars should be conducted at a temperature 1<
11500. The major ferrite formers are C, Cr, Mo,and Ti. The maximum
amount of metastable 0( ferrite is formed on slow cooling to 8500 and de-
pends upon the rate of diffusion of the alloying elements around the carbide
inclusions. The change in the structure of the steel in the process of aging
at 6500 is' attributable to the formation and growth of carbides, Of.,the
.1
M023C6 type. E1572 steel becomes less stable in the course of the aging
process and acquires a tendency to formation of C~ ferrite. Aging of the
steel consists of the -precipitation of a carbide phase (Nb, Ti)C and (Cr,
Ni, Fe, MO, W)23C6 , and sometimes due to formation of a (7 phase of
the (Cr, Mo)Fe type.
V.R.
1, Steel-Transformations-Effeots of forging 2. Steel-Deformation
Card 2/Z

J J_ A" r, 137-58-2-4078
Translation from: Referativnvy zhurnal, Metallurg-Aya, 1958, Nr 2, p 259 (USSR)
AUTHORS: Lashko, N.F., Tseytlin, V.Z.
TITLE: Certain Peculiarities of Medium-carbon Chrome -molybdenum
Pearlitic Steel (Nekotoryye osobennosti sredneuglerodistoy
khromomolibdenovoy perlitnoy stali)
PERIODICAL: V sb.-. Fiz.-khim. issled. austenitn. splavov. Moscow,
Mashgiz, 1957, pp 167-171
ABSTRACT: A study was made of two types of chrome- molybdenum steel
containing 2 percent Cr and 0.9 percent Mo, one with an 0.5
percent V content and one with no V content. The steel was fused
in a high-frex~lency furnace with a capacity of 12 kg. The ingots
were forged into rods which were normalized at 10000 C and
tempered for 6-: 10 hours at 650- 7400 and for 100 hours at 6500 -
The phase comp6sition of the steel was investigated by means of
a comprehensiveiphysicochemical analysis which involved sepa-
rating out the su4plus phases by chemical means, a chemical
analysis of the residue, and a differential X-ray and chemical
study of the residue phases. After normalization and tempering
Card 1 /Z at 6500 for 10 h,)urs the steel with no V in it was found to

137-58-2-4078
Certain Peculiarities of Mediurn-carbon Chrome -molybdenum Pearlitic Steel
possess three phases of varying composition (Fe, Cr, Mo) 3C, (Mo, C r) 2C,
and (Fe, Cr, Mo) 23C 6 ; the steel with the 0.5 percent V content was found
to have two phases (Cr, Fe, Mo, V) 7C 3 and (V, Mo, Cr)C - In the steel
with no V the (Fe, Cr, Mo) 3 C phase was not in evidence after a 100-hour
tempering at 6500 , which suggests that this phase is metastable. The com-
position of a stable phase in the steel with no V was not ascertained. In the
V-based MeC phase of a V-containing carbon steel the Fe was practically
insoluble, the Cr was not very soluble, but a relatively large quantity of
Mo could be dissolved therein. A small quantity of V ( e-00.5 percent) ,
which was almost wholly combined with the vanadium carbide, exhibited great
influence on the phase composition of the steel. Because a significant quantity
of the Mo combined with the vanadi-,.:.m carbide, the possibility of formation
of Mo 2C was excluded. The remaining C combined in the phase Me 7C 3'
T.F.
1. Steel--Phase studies
Card 2/2

AUTHOR: LLSHKO,N.F.~ LASHKO-AVAKYAN,S.Y. PA - 216o
TITLE: The e~_EBY~g'cal Strength of a Welded Joint in the Crystalli-
zation Process. (Tekhnolo.-icheakaya prochnost' svarnogo
soyedineniya. v protsesse kristallizatsii, Russian)
PERIODICAL: IzveBtiia Akad.9auk SSSR, Otdel.Tekhn. 1957, Vol Nr 1,
pp 103-114 (U.S.S.R.)
Received: 3 / 1957 Reviewed: 4 / 1957
ABSTRACT: The technological strength of a welded joint during a welding
process is investigated. It is shown that, for explaining me-
chanical characteristics of a body cooling down in the solid-
liquid state, it is sufficient, in the case of not high deforma-
tion-velocities, to proceed from the properties of the solid
crystalline body, while the resistance of the liquid phase
against elongation may be neglected. In the case of welding by
melting the peculiarities of crystallization must be taken into
account. In the course of crystallization also the section of the
melt to be welded in the zone of thermal influence participates
in the process. The change of the strength of the melt occurs
spontaneously without any exterior action. Destruction of the
welding seam in solid-liquia form takes place with the partici-
pation of deformations by elongation. Experiments showed that,
in the case of malts of the euteotic type, the width of the inter-
Card 1/2 val of crystallization depends essentially on the composition

PA - 2160
The Technological Strength of a Welded Joint in the Crystalli-
zation Process.
ASSOCIATION:
PRESENTED BY:
SUBMITTED:
AVAILABLE:
of the melt and on the velocity of crystallization. In melt-
systems with the formation of inconstant chemical compounds,
peritectic reaction cannot develop to the end if cooling is
rapidp and crystallization ends by the formation of a small
quantity of a labile eutectic. The occurrence of the latter and
the drop of temperature on the occasion of the joining of the
dendrites on the occasion of the crystallization of these
melts is the reason for their pronounced tendency to form a
crystallization gap. It may be assumed that part of the melts
of the system under investigation undergoes periteetie reaction.
(8 illustrations and 2 tables).
Not given
22. 6. 1956
Library of Congress
Card 2/2

/ L--- /K
,q Ce, ( /:
107.WVA,M.N.;
LASHKO, N.F.
.
Binary carbides containing silicon. Zhur. neorg. khim. 2 no.11;
2517-2519 N '57. (PDU 11:3)
(Carbides) (Silicon) (Alloys)

5 HKD., Y
.~60ncerning.the incr
ease of the Strength of Spot Welded Joints
of 1,iB Alloy," by Candidate of Technical Sciences A. Jai. Andre-
yev and N. F. Lashko, Metallovedeniye i Obrabotka Metallov, No
3, Mar 57, pp 50-55
The strength of spot welded Joints of the magnesium alloy, MA8, with
A''I thiclmess of 3 mm, under static, repeated-static, and vibrational load-
_~.ings is studied. 'The welded Joints with working and joining points, and
-also siailar riveted joints, were subjected to comparative tests. The test
:',p1qces were welded by the most favorable means on a machine (mvps-6ou) with.
la.~._direct current impulse. The diameter of the fused ;ore of the spot con-
:,:sisted on the average of about 10.5 mm., and the depth of the fusion was
~held within the limits of 50-60%. The welded and riveted test piecec were
statistically of equal strength.
It vas found that the strength of the welded joints (especially with
,.vbrking points) is considerably below the strength of the basic metal, The
-breakdown of the welded joints with the working points occurs at the border.
of the fused core or in the zone of transition. The single t pe riveted
Acint broke,downat the section weakened by th-e-hole.

For increasing the strength-of the welde d joints the IVeld spots were
,.subjected to single and multiple pressures in the interval above the elas-
-,,t:ic limit and the conditional yield point of the alloy. The pressures were
,,exerted by steel dies with an operating surface slightly larger than the
surface of the electrodes.
Thus there exists a real possibility of increasing the vibrEtional
.strength of the welded points of joints in MA8 alloy by means of treatment,
of'~.the-~ i4eiA 4 ad. (U)
e iainks with stE itic pressure, relatively low Io

A Cl I/ Al"
AUTHORS: Laswt:o 5 N. F.) and Rodiiial, Ye. Ya. 126-2-11/35
TITIS: Distribution of alloyinF3 elements in austenitic
chromiwn-tungsten stools and alloyc *~,-ith variable
nickel contents. (Raspredeleniye legiruyushchikh
elementov v austenitnykh khromovollframovyk-h stalyakh
i splavakh s peremennym. soderzhani-yem nikelya).
PERIODICAL: Fizika Metallov i Metallovedeniye, 1957, Vol-5, No.2,
pp. 261-267 (USSR)
ABSTRACT; Nickel is one of the main elements~ contained in austenitic
steel which brings about a thermally stable austenitic
base of the solid solution. The nickel and the iron
possess differing carbide forming abilities and, therefore,
different quantitative combinations of nickel and iron in
steel should have a predominant influence on the
solubility of carbide forming elements in the solid
solution. In this paper the results are given of the
phase analysis of austenitic steels and alloys. The
steel and alloy specimens chosen contained the following:
0.2% C1 18% Crj 9% W, 1 to 4% V, 1 to 4% Nb and,
respectivel-, 24, 42 and 1~3% Ni. The alloys were cast
into ingots weighing 4 kg quid the sBecimens cut out from
Card 1/4 these ingots were all heate' at noO C for five hours,

126-2-11/35
Distribution of alloying elements in austenitic chromium-tungsten
steels and alloys with variable nickel contents.
quenched in oil and then aged for fifty hours at 8000C.
The anodic precipitates,separated from the all6ys in
the electrolyte were subjected to X-ray and chemical
analysis. The electrolyte consisted of a solution of
300 9 KC1 + 10 cm HU per one litre of water; the
electrolytic decomposition of the precipitates was
effecY at room temperature using a current density of
1 A/cm . Almost the whole of the nickel content in all
the three types of alloys was in the solid solution and
only very small quantities of it were detected in the
precipitates (from 0.02 to 0.1% of the dissolved metal).
The results of phase analysis are compared with the
results obtained for lon- duration strength. It was
found that an increase of the nickel content in the steels
and alloys reduces the carbon solubility in them and,
accordingly, brings about a change of the solid solution,
of the composition of the separated out phases and of
the heat resistance. In alloys not containing W, V and
Nb (0.2% C; 18.5% Cr and a variable Ni contend) only one
carbide forms, namely (Cr, Fe, Ni)23 C6' Addition of V
Card 2/4 or Nb to such alloys brings about formation of special

126-2-11/35
Distribution of alloying elements in austenitic chromium-tungsten
steels and alloys with variable nickel contents.
carbides of the type MeC (VC,NbC) containing a certain
quantity of Cr. The graphs Fig.1 show the influence of
Nb on the chemical composition of the carbide precipitates
of cast alloys containing respectively 18, 24, 9% W;
201 40, 9016 W; 20, 60, 9% W. The graphs Fig. 2 show the
influence of V on the chemical composition of the
carbide precipitates of cast alloys of the same types as
Fig.l. The Tables contain numerical results of the phase
analysis, of the changes in long duration strength of heat
treated alloys with various Ni contents, of the phase
composition of the residues separated out from heat treated
alloys containing various quantities of Nil Nb and V
as well as the results of X-ray structural analysis of the
Me C phase for an alloy containing 58% Ni and various
qu3~tities of V and data on the influence ofo Nb and V
on the long duration strength of steels at 800 C. In
alloys containing 20,06 Cr, 60% Nil 9% W addition of 1 to 4% V
brought about formation of the primary carbide of the type
Me C based on the metastable carbide Cr2C containing
V Ed W. It can be seen from the graph, Fig.2, that the
Card 3/4 quantity of V enterinG into the solid solution increases

126-2-11/35
,Distribution of alloying elements In austenitic chromium-tungsten
steels and alloys with variable nickel contents.
continuously with increasing V content in the alloy and
this brings about an increase in the thermal stability
of the solid solution. The total quantity of the elements
entering into the graphite phase changes relatively
little. However, with increasing V content in the steel
the relative quantity of binary carbides increases and
these are more stable than the cubic carbide of chromium.
An increased hardening of the solid solution with increasing
V content In the steel and also formation of thermally more
stable carbides leads to a gradual increase of the long
duration strength of the steel. There are 2 figures and
10 tables.
SUBMITTED: June 21, 1956.
ASSOCIATION: All-Union Scientific Institute for Aviation Materials.
(Vsesoyuzn nauchno-issledovatellskiy Institut avlatsionnykh
materialov~-
AVAILABLE: Library of Congress.
Card 4/4
t4 /V
AUTHORS Blok, N.I., Lashko, N.V., 32-&-3/61
Sorokina, F.F.
TITLE The Phase Analysis of Chromium-Nickel-Titanium
Steels with Intermetallic Binding.
(Fazovyy analiz khromonikeAitanovykh staley a
intermetallidnym upr6chnerliyem.)
PERIODICAL ""avodskaya Laboratoriya, 1957, Vol. 23, Fr 8, pp-901-903
(USSR)
ABSTRACT In the paper a now method of the eleotrolytical distribution
of phases in steel types with intermet'allic binding is
shown. A typical kind of steel (0,05% C; 111,45 % Ni; 2,53 %
Ti; 11,65 % Or; 0,85 % Al; 0,02 % B) was used as testing
object. The action of the pH of the solution, temperature and
current density were investigated. The following best
suitable electrolysis conditions for the separation of
quantitative anode precipitations were determined: current
density 0,05 a/om2, temperature of the tank 4 100, pH from
2,2 to 4,9. In order to avoid oxygen separation on the
anode 104 CH OR was added to the tank. The concentration of
copper sulfaie should not exceed 5 % because of the in-
crease in acid development. For buffering the solution
CARD 1/2 8 % triply substituted ammonium citrate is added. The

1 1, R " V, K (;""w - C--,
AUTBOR 3 BLOK9N.1.9 KOZLOVAqUoNo, LASHKO N F # and SHPUffqK*YA9 Pk - 2743
-3`
~-
th
B C
IF
M
;
TITLII On
ompound in
SI
0:
O
O
Alloys.
e Ni3
(0 26yedineau NI D Y splavakh nikel-borg Russian).
L
i
PUIODIUL& u
Doklady Akad#mLi
SSSR, 1957, Vol 1139 Ir 4t PP all - 812

Receivedt 6 / 195T Review"& 6 / 1957
AWRACT# The double diagram of the state NL-B (up to 20 % S) was constructed
for the first time by GINBEMHAUS]Mp who found that the compound with
the highest content of nickel is NI2B. KIESSLIR sentiones, also the
high content of niakel of the alloy Ki B without,giving its character-
3
t-intlaso The authors i3mostigated the structure and the phase composition
of Ni-S alloyst which contain 0901 - 295 % 3- littallographloallv they
found that a uniformly Ochable aone is separated at the boundaries
of grax%latloz which form an outoctio with nickel. The alloy with
295 B is pro-outeatica This phase was inoulated chemically is well as
el*otrolytically in &quo*= (10 g (" 4)2 804w4,30 g hydrochloric
hydroxylamin per 1200 al water) end nou-Squeo,29150 KI RU -Per 1150 al
methanol) eloatrolyt. From the data contain" Iitalbles I - 3 it my
be soon that on the occasion of the electrolytic separation of phases
a considerable part of nickel is dissolved baricallyo The major part
in conserved when the alloy to treated with sulphurio acido In w
Card 1/2 oeseprocipitstion shown one and the same phasep i.9. Hi B,
3

On the Irl 3B V,~Rmpound in Mickol.Boron &,,.Iloys.
P1 - 2743
It In a blaakg solid substanoaq insoluble in sulpharic acid (1s2
solution) and,:,olvable after prolonged beating in ooncentrated sul.
phurio &old ( 4)o Whus It =q be said that in the double system
Hi-B there exist* a chtnioal oompound NJ 2B which forms an eutectio
with a solid solution an a nickel basis.
(2 Illustrations and 3 tables)
AOSSOCIATIONs
PIMMO BYs
BUBKMHD&
AVAILLBLIs
All-Union Scientifio Research Institute for Aift;%ft Material
SoIoVOLFKOVICS9 Member of the Acadomy
Library of Congress
Card 2/2

F~,S 14 1-,- 0, N -
PHASE I BOOK EXPLOITATION SOV/3711
Lashko-Avakyan, Sofiya Vasillyevna, Candidate of Technical Sciences,
and Nikolay Fedotovich Lashko, Candidate of Technical Scie'neee
Payka alyuminiye spELavov (Soldering of Aluminum Alloys) Moscow,
1958. 25 P. 7sni-es: Peredovoy opyt proizvodstva, Seriya
"Mashinostroyeniyep" vyp. 14) 5,000 copies printed,
Sponsoring Agencies: Moskovskiy Dom nauchno-tekhnicheskoy propagandy
imeni F,E, Dzerzhinskogo; Obshchestvo po rasprostraneniyu politi-
cheskikh i nauchnykh znaniy RSFSR.
Ed,: S.F. Filippova; Tech* Ed,: R.A. Sukhareva.
PURPOSE: This book is for solderers, .
COVERAGE: The book discusses the difficulties in soldering aluminum,
the methods of soldering and various solders for aluminum alloys
for soldering in the temperature range up to 400*C and from 400
to 620*0. There are 12 references: .3 Soviet, 6 English, 1 German,
and 2 French*
Card 1/2

Soldering of Aluminum Alloys
SOV/3711
TART OF CONTENTS:*.: None given [book divided as follows):
Preparation of product for soldering 8
Soldering of aluminum and its alloys at temperatures up to
4oo0c 10
S61dering of. aluminum and its alloys in the temperature range
from 4oo to 62000 19
Bibliography
AVAILABIX: Libr~ary of Congress
Card 2/2
27
VK
/mg
6-&6o

AUTHORi Lashko, N.F. , CarxUft-~e of Tbahaical Sciences 12 5; - 5 6 -I
TITLEs To the Problem of the Effect of Niobium on the z3triicture o''
Nelda on Austenitic 16-8 Grade Steel (Y, voprosu o v1iyan2_
niobiya na strukturu svarnykh shvov na austenitnoy stal-4
"18-8)
PERIODICAL: Avtomaticheskaya Svarka, 1956, Nr 6, PP 84 - 87 (USSR)
ABSTRACT. The author discusses the effect of niobium in welds or. 'Ili-8'!--
steel as indicated by literature (Guterman, Binder) and ob-
tained by his own experiments. He investigated statements on
the phase-composition of such steel
alloyed with niobium, made
-
by G.G. Mukhin and N.Yu. Pallchuk LIRef. f, who claimed to have
discovered an inter-metallide "N-phase". This theory is refutedl.
There is 1 table and 5 references, 3 of which are Soviet, and
2 English.
SUBMITTED: June 26, 1957
AVAILABLE: Library of Congress
Card 1/1 1. Steel-Welding 2. Niobium-Effectiveness

-IUTFORSt Lashko, N.F., and Lashko-Aval-yan, S~V. SOV-125-58-9-14/14
TITLE. The Role of Carbide Phaz3es and Initial Ferrite in the Formation
of Crystallization Cracks While Welding Austanitic Steels (0
roli karbidnykh faz i pervichnogo ferrita v obrazovanii kri-
stallizatsiornykh treshchin pri syarke austenitn,,rkh staley)
PERIODICAL: Avtomaticheskaya svarka., 1958, Nr 9, pp 98-110 (USSR)
ABSTRAM The effect of alloyinL; on the proneness to crystallization
cracks in welded austenitic steels is disoussed~ Basic fac-
tors determining suoh proneness of weld joints, connected
with alloying of the seams, include the effects of alloying
elements cr. 1) chanEes in the crystallization interval cf
austenitic steels; 2) f:)rration of a non-equilibrium fusible
eutectic between the dendrite axes and at the rain borders;
3) s%rinkage phenomera in crystallization; 4) the initial
grain size, forming during crystallization; 5)C - ferrite
formation in crystallization of austenitic steels, The
effect of carbon, chromium, nickel, silicon, tungsten,
molybdenum, titanium, vanadium and niobium on proneness to
crystallization cracks in austenitic steel i3 analyzid, It
is stated that intermet-allic phases, formed in thG case of
Card 1/2 a considerable content of alloying elements (such aEt tun st
. -en,

SOV-125-58-9-14/14
The Role of Carbide Phasez and Initial Ferrite in the Formation of Crystal-
lization Cracks i7hiie Welding Austeritic Steels
titanium, niobiam and aluminum) do not have a substantial
effect on crystallization crack formation, rhereas carbide
and boride phases are of basic importance. In pure austenitic
steels, in particular in the case of a columnar strucTure,
vanadium, t-itanium and niobium can increase proneness to
crystallization oracks; in the case of a bi-phase structure
+ created by these cr other ferrite-form-ing elements.
such as chromium, mollybdenump tungsten and s4licon, proneness
to crystallizatic-n cracks can be depressed. The positive
effeci of an initial ferrite phase in austenitic steels on
their sensitivity to czystallization cracks is explained by
taking into adccuilt the effect of the ferrite phase, on the
aforement-ioned basic factors.
There are 5 microphotos~ and 13 references, 11 of which are
Soviet and 2 English,
SUBMITTEI)i Julie 14, 1957
1. Steels---Fracture 2. Weldip-g--Metallurgical effects 3. Steel
--Crystallization 4. Steel--Properties
Card 2/2 USCONIV-D13-55,67,14

SOV/24--58-12-15/27
AUTHORS: Blok, N.I., Glazova, A.I., Lashko, N.F., and
Yakimova, A.M. (Moscow)
TIT1.3; Influence of Hydrogen on Structural Transformations in
Titanium Alloys (Vliyaniye vodoroda na strukturnyye
prevrashcheniya v titanovykh splavakh)
PERIODICAL. Izve stiya Akademii NaWc, Otdelen3*- e Tekhnicheskikh
Nauk, 1958, i4r 12, pp 96--99 (USSR3
ABSTRACT: The influence of hydrogen on the plastic properties of
titanium alloys, which has recently been widely studied,
varies with the form of the titanium in -the alloy. The
object of the worK described was to i.-u-irestiga-te the
influence of hydrogen on szructural transformations in
alloys vrith an :--\. + 0 solid solution structure. Alloys
VT3 and W13--1, were studied, their respective compositions
being: 0.04, 0.046% C; 2.76, 11.93% Cr; 4.9, 4.6%o Al;
1.5% Mo; 0.20~ 0.2LI.,," Fe- 0.04, 0.027% Si;
0.10, 0.11% 0; 0.028, 0.04.2,"/o N. The method used
consisted of the non-aqueous electrolytic separation
of phases, -~kose, structvres were then investigated with
V_ -so studied metallographically.
". rays. The alloys wero a.L
Card 1/3 Saturation with hydroGen %,ias effected by sealing the

SOV/24-58-12-15/27
influence of Hydrogen on Strnicz-arai Transfor tions in `_'ita"r_J_.=
Alloys
cylindrisal Specimen and titanium hydiide in an
evacuated quartz tube and heating to 7OOrIC for 10 hours.
Specimens wi:".h 0.005, 0.015, 0.025,, 0.035, 0-05 and
0.12 wt..%o hydrogen were obtained. They were subjected
to differing heat tx-eatments. It was found that in the
VT3 alloy containing 0.01 -~5-0,03113,5,o' hydrogen tha
eutectoid.al raaetion P-) o~ + TiCY2 'S faster than in the
hydrogen-free alloy; wit-h 0.05-0.060% hydrogen the
0-phase fc-n-as titanluia _uydride on heating; with
0.12% hydrogen the res-idual. ~-.phAse is stabilized and
there is no eutectoidal X,:,a(-.tion either on cooling after
annealing or o7a heating for 100 hours at 4-00-4500C.
9
In the V1113-1 alloy coln*uainiaag L,,_,ol-,.~bdenum the residual
P-phase did not decompose afruer -innealing and heating
at 400 and 4500C for 100 -hou-Is irrespective of the
hydrogen content in th,:-. ran.Gp st-Ldir5d. In both types
of alloy the O-phase unit --ell paraiieter in--reases with
hydrogen rontent (Fig.1 shows thiz- effect for the -VT3-1
Card 2/3 alloy heat.-treated in various ways). During the heating

SOV/24-58-12-1-5/2?
Influence of Hydrogen On Strur;-Uural Transformations in Titanium
Alloys
of both alloys at, 400-45000 the residual 0--phase is
enriched in chromium and molybdenum amd, possibly,
loses hydrcgen. There are 3 figures, 3 tables and
6 referencezi of which 5 ana English and- 1 Soviet.
SUBMITTED: 8th August 19c?.
Card 313

0
AUTHORS: Blok, 11. 1., Glazzova, A. I., Kokhova, G, M. 52-2-6/60
L a a hkaJL~-F -
TITLE; The Phase AnalYsis of Comp-, -ex Titanium Alloys
(Fazovyy analizz s1c-,hnoleCircvannyk1h titanovykh splavov)
PERIODICAL: Zavodskaya Laborator~-,-a, 1915, Vol. 24. Nr 2, p:~. 141-145
(USSR)
ABSTRACT: In an earlier work various technical titanium alloys
contai-ni-"G all=Lnium, cl-iromium, molybdenum and changing
amounts of hydro[.-ert were already investi-ated, as -aas the
phase composition of azoticized titanium. For the separation
of phases a r-ethod of t-'(:..e zcnodic deccmposit-Jon of alloys
was developed. The authors rforked with potassium zhodanide,
citric acid. lyce-2-*n and m-ethano", a-' a cur-rent density
of 0,013 A/C terminal voltage of 30 V, at from -70 -
-100C. After the 'the i~,-.iade precipitates were
investiEated chemi(;ally as well az; radicgraphd-,ally. In
earlier works the T--alli:,Ys had been. smelted in graphite
crucibles, the carbon disturbing further investiGations;
Card 1/3 therefore the author-2 smelted twD-to threetimes ii~i. are

The Phase Analysis of Complex Titanium Alloys 32-2-6160
furnaces (till homogenization occured). The radiograms of
heat after-treated (1, 10; 50 hours at 5000C) anode deposits
showed the metal stable a-phace while the CO -phase Teas no'..
observed. The changes in the a8ing process of the P-phase
of two technical alloys (5,108% Al~ 3,06~ Cr and 4-71ela A17
1.86,ifo cr, 1.55 11 Mo) were put down in a table and the authors
noted that after an a 'Ing at 4500C only the P-phase is
observed while the elatectoid reaction P - a + Cr2Ti did not
take place. Titanium hydride was isolated for the first time
and the authors found that hydroUen dissolves mainly in the
P-phase (this was found in collaboration with A. T. Yakimova),
if, however, there is no such phase the excess hydrogen then
forms the titaviuza hydridea. AccordinC to radiceraphis
structural analyae3 the T-4-hydride was of crystalline
structure af the HaCl-type, while the neutron-diffraction
showed a tetraGonal structure. The analyses of the anode
precipitates treated in a nitrogen current at high temperatures
showed that theq consist of one or two phases, 'he wellknown
finely Crained TiN and in lovier layers the second nitride
Card 2/3 TinN. The latter i_- of tetl-afgonal 3tructure. The -4--vestIgations;

The Phase Analysis of Complex Titanium Alloys 32-2-6/60
of Palty, Margolin and Fielsen concerning the Ti-21 system
in the 9 -phase showed a similar structure, the difference
however, between the radiograms found by them and the
radiograms of the present work, is considerable.
There are 5 tables, and 3 references, 1 of which is Slavic
AVAILABLE: Library of Congress
1. Titanium alloys-Phase studies
Card 3/3

180), 5W
AUTHORS: Blok, N. I., Kozlo-~a, I.I. IT., Lashko, IT. F., SOV/32-24-11-44i37
Andreyeva, A. G. 11_~
TITLE: Phase Analysis of Nitrided Steels (Fazovyy analiz azo-
tirovannykh staley)
PERIODICAL- Zavodskaya Laboratoriya, 1958, Vol 24, Rr 11,
Pp 1315 - 1319 (USSR)
AB~TRACT: To study the many kinds of corrosion resistance of
nitrided surfaces of rust-resistant steels an anL-
lytical method was developed, and the phases and the
distribution of the alloyed elements were invest-I.-ated.
The experiments were carried out on 251=8N�V2 steel.*
with the participation of 1`131.Rudneva, chief en~;ineer.
X-ray structural analysis showed two phases on the
surface of the nitrided layers: the Fe 21f type v;ith a
hexagonal crystal lattice and the CrIT tv-e v,,ith
a cubic lattice. The phaaoes could be&t-be,separated with an
electrolyte consisting of 50 ml. HC1 (d= 1.19) and 2
1150 ml methanol, at a current density of 0,02r Anpore/rM
Card 113 a temperature of -50 to -100, and over a duration

Phase Analysis of Nitrided Steels SOV/32-24-1111-4137
of 20-30 minutes. The anodic deposition consisted
of iron carbon nitride, chromium nitride, and
chromium carbide. The separation of the chromium
nitride from the iron carbon nitride was carried
out using the method of N.M.Popova (Ref 2). Th~
n1trided amples dissolved in the anodic dissolution
up to 003 5 zOn deep *Up to a depth of 0,17 mm the
nitridea layer c onsisted of three phases: the carbon
nitride of the iron and chromium (Fe Cr)2('1'C),
the chromium nitride CrIT) and the solid solution
enriched with nitro,-en and nickel. This layer pos3essed
a positive electrode potential and was highly resictant
to corrosion. The nitrides occurred at a depth of
0,17 to 0,22 mm and the li-ye-r consiated of Fe N,Cr'114,
Cr 23 CP and the solid solution. The nitrogen ion-
centration was 0,3 - 0,4%, the electrode potential
negative, and the corrosion resistance decreased. In
the still deeper layers the chromium content was 15%
with only 3% present as the Cr 23C6' It showed a
Card 2/3 positive electrode potential and a high resistance to

"37
Phase Analysis of Nitrided Steele SOV/?2-24-1
corrosion. Invcstij~.tions on nitrided Armco iron
showed that the nitride phase up to a depth of
0,02) nma consists of Fe 2N and up to a depth of 0,06
of Fe 411. The gent~r,,I' content in the nitride phn~le
was 10-36~,Lq -while the rest was a solid ooli.,.ti-on
There are I fi,3ure, 5 tables, and 1 rcf-~rencc,
which in Snviet.
Card 3/ 3

7 `Vm' `E '~Tl t) I/r: T'
k ), ; - - IJP(C)
AP6-0-2-7-7-87.
ACC NR,
JD11 1?iIJ-G,
URtOi261661022100
SOURCE CODE:
AUTHORS Lashko, N. F,; Sorokina, K, P,
ORG: none J
TITLE: Characteristic features of the phase Composition of ~at-
resistant $tools and alloys of the Fe-Ni-Cr-Ti-Ho-W B a tem
SOURCES Fiz1ka metallov I metallovede'niye, v. 2 , no. 1, 1966, 66-72
TOPIC TAGS: heat resistant steel, alloy steel, heat resistant alloy,
nickel chromium alloy, molybdenum containing alloyp tungsten can-
taIninR alloy, boron containing alloy, alloy aging, phase compoo.ItLon
ABSTR#fT: The phase composition of heat-resistant E1696, ~16964. and:"
E1787-iteels has been Investigated. Electrolytic a11 -1-solated_ pre-
cipitates were found to consist of TIC carbidep TIB41and M03B2 borides,
-Ni3TL phase n amounts'
FeZTL and Fe2 (TI, Mo) compounds, and 0
depending on steel type and temperature and duration of aging. The
0-Ni3Ti phase precipitates in a cubic shape at 'temperatures above
750-800C. However, lamellar partLcles of this phase precipitated
at grain boundaries in E1696M steel after aging at 730C for 2000 hr
0r in E1787 steel after aging for 6000 hr. With prolonged-aging,
8-N13TL phase of 91696M steel becomes richer In-.Iron. Precipitation of
Card 1/ 2 UDCt 669.14.018.451620.181.4

L 42137-66
ACC NRi AP6027787
the FQ2Ti phase in E1696 steel occurs at a lower te-AperatureIa~out
800C, and in larger quantities than in E1696M steel. Precip it ,on
of the F82Ti phase in the latter steel occurs only after agingNt
900C for 100 hr or at 750C for 2000 hr. The phase composition of
E1787 steel generally is similar to that of B1696M steel, except that
in the fOrMOTO N13 (Tit Al) replaces B-H13Ti phase. The tendency of
8-N13Ti phase and N13 (Tit Al) phase to transform from globular to
lamallar form at high temperatures or after prolonged aging is typical
for many Ni-Fe-Cr-Al oyaten alloys. Orig. art. ban: 1 figure and
7 tables# JTDJ
SUB CODEt It/ SUBH DATEi 03Aug64/ ORIG REFt 006/ ATD PRESSt

L 14 -x
Is.
N nit
I T
10 1 h, 9 1
1
Sam,
av
a ;z
.
pit
av
- ~131
31311 8
lip; Wli I~1 g F I I c
114, .11 V Af
2 , 41p
AAV vif -0, b- 4.
11 J118!1M,
Mus 11 Ila
jai
v all

25(l) PHASE I BOOK EXPLOITATION SOV/2212
Lashko, Nikolay Fbdorovich., and Soflya Vasillyevna Lashko-Avakyan
Payka metallov (Brazing and Soldering of Metals) Moscow, Mashgiz, 1959. 442 P
10,000 copies printed.
Ed., S. L. Martens,
Engineer; Tach. Eds.: A.F. Uvarova and V.D. ElIkind;
"ging Ed. for Literature on Heavy Machine Building (Mashgiz): S. Ya.
Golovin, Engineer.
PURPOSE: This book is intended for scientists, engineers, and technicians con-
cerned with the development and application of metal soldering in the machine-
building industry.
COVERAGE: The authors discuss the basic physical and chemical processes and
structural transformations occuring during metal soldering and brazing, the
constructional characteristics of soldered joints, and the preparation of
parts for soldering. They also give information on fluxes and solders and
describe methods for manual and mechanized soldering of alloys of different
bases. No persona3-ities are mentioned. References follow each chapter.
Card l/ 9

Brazing and Soldering of Metals (Cont.) SOV/2212
TABIX OF CONTENTS:
Foreword 3
Introduction 5
PART I. BASIC DESIGNS OF SOLDERED JOINTS
Ch. 1. Types of Soldered Joints 9
I. Basic types of soldered Joints 9
2. Specific design features of soldered butt, Joints, lap Joints,
and scarf Joints for continuing parts 10
3. Specific design features of soldered fillet and tee Joints of
intersecting parts 14
4. Specific desiga-features of Joints, where the soldered parts
are tangent 17
5. Requirements for the distribution of the solder before solder-
ing 17
Ch. II. Capillary Space in Soldering and Soldered Joints 22
PART II. PHYSICAL AND CMWCAL PROCESSES TAKING PLACE DURING
SOLDERING AW 91M DETEMUNING, PROPERTIES OF SOLDERED JOINTS
Card 2/ 9

Brazing and Soldering of Ketals (Cont.) SOV/2212
Ch. III. Processes Taking Place During the Formation of a Soldered Joint 28
1. Processes determining the filling of the clearance in a joint
being soldered 28
2. Diffusion between the liquid solder and metal being soldered 37
3. Crystallization of the joint during soldering 39
4. Formation of solid solutions and chemical compounds during
soldering 44
5. Processes of entectic crystallization during soldering 47
6. Effect of gases on soldering processes and on the quality of
the soldered joint 51
Cr--. IV. Decay of Parts During Soldering Caused by Application of the
Liquid Solder While Parts are Being Subjected to Stress 54
PART 111. SOMERS AND FLUXES
Ch. V. Solders With Various Metal Bases 65
1. Bismuth-base solders 73
2. Iadium-base solders 75
3. Tin-lead and tin-zinc solders 76
4. Lead-base tinless solders 83
Card 3/9

Brazing and Soldering of Metals (Cont. SOV/2212
5. Codmium-base solders 86
6. Low-melting creep-resistant solders 87
7. Zinc-base solders 91
8. Magnesium-base solders 94
9. Al-aminum-base solders 95
10. Silver-base solders 98
11. Copper-base solders log
12. Gold-containing solders 117
13. Nickel-base solders 119
14. Iron-base solders 122
15. Solders for soldering without flux 122
Ch. VI. Flu-m-as for Soldering Metals and Alloys 129
1. Fluxes for soldering with low-and high-melting solders 132
2. Gas fluxes 155
3. Removal of fluxes after soldering 156
PART IV. METHODS OF SOLDERING METALS AND ALLOYS
Card 4/9

Brazing and Soldering of Metals (Cont.)
Ch. V11. Cleaning and Preparing Surfaces for Soldering
1. Methods of cleaning and degreasing surfaces
2. Mechanical method of removing scale and oxide films
3. Chemical methods of removing scale and oxide films
4. Preparation and metal-coating Of surfaces
Ch. VIII. Working With the Soldering Iron
Ch. DC. Soldering in Liquid Media
1. Soldering in baths with fused salts
2. Soldering aluminum and its alloys in flux baths
3. Soldering in baths with fused solders
Ch. X. Soldering in Furnaces
1. Preparation for f'urnace soldering
2. Equipment for furnace soldering with fluxes
3. The process of furnace soldering with fluxes
Ch. XI. Soldering With Torches and Gas Burners
SOV/2212
163
163
165
107
176
183
191
192
200
2.02
2og
210
213
214
217
Card 5/9

Brazing and Soldering of Metals (coat.)
1. Torch soldering
2. Blovtorches
3. Soldering with welding and soldering torches
Ch. XII. Soldering Methods Employing Electric Heating
1. Soldering with induction heating
2. Electric-resistance soldering
3. Soldering in electrolytes
4. Electric-are soldering
Ch. XIII. Thinning and Wiping
Ch. XIV. Ultrasonic Soldering
sOV/2212
Ch. XV. Brazing in Gas Atmospheres
1. Fundamentals of brazing in gas atmosphere with a low partial
pressure of oxygen
2. Brazing in vacuum
3. Brazing in neutral gas atmospheres
218
22o
221
226
226
237
246
253
257
261
270
270
279
284
card 619

Brazing and Soldering of 14etals (Cont.)
SOV/2212
4. Brazing in reducing gas atmospheres 286
5. Composition and production of reducing agents containing
hydrogen 294
6. Equipment and technological methods for brazing in reducing
gas atmospheres 298
7. Reducing gas atmospheres without hydrogen 310
Ch. XVI. Reaction and Mffusion Brazing 315
1. Reduction of solder during brazing 315
2. Contact brazing 318
.3. Diffusion brazing 322
Ch. XVII. Braze Welding 325
Ch.. kVIII. Inspection of Soldered Joints 329
PART V. SOLDERING METALS.AND ALLOYS OF VARIOUS BASES
Ch. XIX. Brazing Iron and Iron Alloys,, Carbon and Alloy Steels
and Cast Iron 339
1. Brazing carbon and lov--alloy steels 341
Card 7/9

Brazing and Soldering of Metals (Cont.) SOV/2212
1. Soldering aluminum and aluminum alloys 394
2. Brazing magnesium and magnesium alloys 416
3. Brazing beryllium 421
Ch. XXVI. Soldering Low-Melting Metals and Their Alloys 425
1. Soldering zinc and zinc alloys 425
2. Soldering lead, tin, and cadmium 426
Ch. XXVII. Soldering Glass and Ceramics to Metal 428
AV,kILABIE: Library of Congress
Card 9/9
GO/fal
lo-12-c59

5(2), 18(6)~ 18(7) SOV/78-4-7-24/44
AUTHORS: Lashko, N. F., Sorokina, K. F.
TITLE: The Phase-analysis of the Copper Corner of the System Copper -
Nickel - Silicon (Fazovyy analiz mednogo ugla sistemy med' -
nikell - kremniy)
PERIODICAL% Zhurnal neorganicheskoy khimii, 1959, Vol 4, Ur 7,
pp 1613-1615 (USSR)
ABSTRACT: The phase composition of the copper corner in the Cu - Ni - Si
system and in industrial Ni-Si-bronzes has not yet been ex-
plained. References 1-4 contain contradictory data. In order
to explain these contradictions, alloys with 1.Z Si and 3, 7,
12 andl 270%o NIL as well as 1.5-5% Si and 20-250%, Ni were produced
(Pig 1). The electrolytic phase separation was carried out in
electrolytes consisting of aqueous solutions of copper sulfate
and ammonium citrate. Current density amounted to 0.05 a/cm2.
Table 1 shovis the X-ray structural analysis by means of K 2-
radiation of copper for the precipitates obtained from alloys
containing 1-% Si. In alloys rith 1.5-5,4- Si and 20-25:~ Ni the
phases N'3Sj and Ni 53i2 were founds Chemical analyses of the
'
'
Card 1/2 5'
10
hi aft;Ur
precipitates of alloys I'llith 1
12
a
and 20
Si and 7
.
,
,
;
i

SOV/78-4-7-24/44
The Phase-analysis of the Copper Corner of the System CODDer - Nickel -
Silicon
various thernial treatments are given in table 2. The precipit--tes
consisted of the phases Vi.5 Si 2' 11'3 Si and a-Ili2Si. All phases
were free from copper. In alloys of up to 7;fo Ni the solid
I Si. In alloys
solution is in equilibrium with the phase a-1111.2
with 12yo 11-4 the equilibrium phase was Ni 5Si 2 at 500-7000, and
in alloys with 20-25%o K it was the phases Ni 5342and 11.13Si.
There are 1 figure, 2 tables, and 5 -references, 3 of which
are Soviet.
SUBMITTED: April 12, 1958
Card 2/2

SOV/129-59-5-12/17
* G~N, O~--:--kho-
AUTHORS: M.F. Alekseyen1co. N.F. Lashko, N.M. Pcpcva,
TITLE: Phase Analysis of'-IT-eatBesistant Constructiona.1 SteelE
(Fazovyy analiz teplostoykikh konstruktsionnykh staley)
PERIODICAL: Metallovedeniye i. Termicheskaya Obrabotka Metallov,
19595 Nr 59 pp 52-54 (USSR)
ABSTRACT: The authors investigated the phase composition and the
mechanical properties of the steels 1OKh3VA, 30n2N2Vk
.U.e. with differing vanadium contents) and of the steel
EI415. The results of the strength tests after heat
treatment (quenching in oil followed. by tempering) for
each of these steels are entered in a table on page 52-',
The carbide analysis was effected on 12 mm. diameter,
60 mm long specimens which served as anodes and dissolved
in an electrolyte for a duration of 5 hours with a
current density of 0.2 A/cm. , followIng vhJ,,;u the solution
was cooled to 00C. The Fe., Cr, Mn, W, Vai.i Mo contents
of the carbide precip-tates were determir a. In I
L
the influence is graphed of the temP-.,.ng time at 500 OC
of the steels 30Kh2N2-VA (curvas I a 2) and 30Xh3VA
Card 1/3 (curves 3 and 4) or, the contentF of individual elements
which are combined in the carbides-, In. Figs 2 and .1 the

SOV/129-59-5- 12/17
Phase Analysis of Heat Resistant Cons tra r- tional Steel Is
influence is graphed. of the tempering time ar. 600 f-_)f
the steels 301Q-L2N2-VA and. 30.'Qa3VA -,~esp e0avoly or,
c--on*'L:ents of Cr arid Fe whi--h aie ~.owbined In the
cementite and trigonal r--h-rom:1-um caTbide; h e 9 f f 'Q, (i
vanadium add-ition-q on the mechani~--ai propertlas and f-h~?
sustained strerig-Lh. of 30hh'e--'N2VA sterel is graph-ed, in Figs
4 and 5. The results of analysis of phas?
30Kh2N2VA steels, with vari-ou-s -,janadium 'contents enablc-d
explaining their beha';iAour in teqts for susta.fried.
strength at 550 OG~ The sustained str-,ngtb Is determin-:,d
by the hardening of, the so"Ad sol-utiork, J.ts tho~,mal
stability and also its interaotion with the Teje,::ted,
phases. The hard.aning effe(;t of the iejecte-d j)haS;,j On
the steel deuend5 or, their d.egre:~ of dispeTl~-Ion and the
proneness to dif fusion -interac-tion with. the solill
solution.; the lower the speed of f-o-Mation and. th~,
slower the growth of the germinatdon.-7, the greater will
be the hardening effac-'!; on the ste"-l.' After tempering at
650 OC the caTbid.e phases in the steel E14-11~; -,ombinecl
only partly with the alloying elements W, Mo, V and C-.-
Card 2/3 The alloying elements which remainGd. in the Eolid

SOV/129-59-5-12/17
Phase Analysis of Heat Resistant Constructional Steels
solution, slowed down diffusion process and hardened the
solid solution. After tempering at 650 OC for one hour
2~2% Cr remained in the solid solution. Subsequent
tempering at 500 OC for 10 and 300 hours had little
effect on the redistribution of the alloying elements
between the carbides and the solid solutions, Such
alloying distinguishes favourably the steel EII+15 froia
other steels of similar composition,
Card 3/3 There are 5 figures and I table.

18(7)
AUTHOR:
SOV/135-59-6-6/20
Lashko-Avak-yan, S. V., and LashIco, N. F., Candidates
of Technical Sciences
TITLTI: Problems in Alloying Welded Strained Aluminum Alloys
PERIODICiU.: Svarochnoye Proizvodstvo, 1959, Nr 6, pp 19-23 (USSR)
ABSTPUALT: For a long time aluminum-alloys have been used for
welded products, with a comparatively small tendency
to fissure-forming, producing plastic, weld seams.
The alloys were AD-1, AMts, AMg-3. The article re-
presents new sorts: Allg-6T, D20, M40, which are differ-
ent from DK6. AK6,1 AK8, B95, according to their struc-
ture. The article discusse *s from the point of view
of improving their weldings welded strained aluminum
alloys used in the welding industry, such as Mts AV,
AMg, Ah6j )Z8, D16, V 95. These alloys contain almost
all technical systems of aluminum- alloys: Al-Mn, Al-Mg,
Al-Mg-Si, Al-Mg-Si-Cu, Al-Cu-14g, Al-Zn-Mg, Al-Zn-Mg-Cu.
Single sorts of aluminum are examined separately: tech-
Card 1/2 nical aluminum, AlIts-alloys, Al-Mg-alloys, AB-alloys,

SOV/135-59-6-6/20
Problems in. Alloying Welded Strained Aluminum Alloys
AK (AK 6Y AIC 8) alloys, Duraluminum DI and D16, alloy
B 95. There are 5 graphs, 1 photograph, 1 table, 1
diagram and 4 references, 3 of which are Soviet and
1 German.
Card 2/2

S/137/61/()00/00,?/016/046
AOO6/AOO1
Translation from: Referativnyy zhurnal, Metallurgiya, 1961, No. 2, P. 9 # 2E69
AUTHORS: Lashko-Avakyan, s.v., Lashko, N.F.
TITLE: On the Weldability of Aluminum Alloys
PERIODICAL: "Tr. Nauchno-tekhn. o-va sudostroit. prom-sti", 1959, No. 33, PP.
3 - 19
TEXT: The authors analyze the mechanism of hot crack formation during
the,welding of Al-alloys of the systems: Al-Cu; Al-Cu-Mg; Al-Mg; Al-Mg-Si;
AI-Zn-Mg and*4-7Zn-Mg-Cu. Problems of chemical heterogeneity and means of modi-
fying weld -jDints are discussed; methods of preventing hot cracIt formation are
recommended.' there are 16 references.
Yu. S.
TranslatoPs note: This is the full translation of the original Russian abstract,
Card 1/1

18(7) SOV132-25-6-5153
AUTHORS: Sorokina, K. P., Blok, 11. 1., Lashkov N. F.
TITLE: Phase Analysis of Chromium-Nickel-Titanium Steels With Inter-
metallide Hardening (Fazovyy analiz khromonikelltitanovykh
staley s intermetallidnym uprochneniyem)
PERIODICAL: Zavodskaya Laboratoriya, 1959, Vol 25, Nr 6, pp 659 - 661 (USSR)
ABSTRACT: It had already been sh017n (Ref 1) that the hardening phase in
the steel type EI-696 is the phase ~ -Ni 3Ti which exhibits
a face-centered crystal lattice. Further phase analyses of this
steel revealed that the two intermetallide phases Fe 2Ti and
o(-Ni3Ti with a hexagonal crystal lattice occur after heating
up to 800-9500. Since also titanium carbide and titanium
boride are present as primary phases, this steel exhibits as
much as 6 phases. An electrolytic phase separation in the
electrolyte Nr 5 (50 g copper sulphate, 80 g triammonium
citrate and 100 ml methanol per 1 1 of water) was carriea out,
and a quantitative separation of the phases IS-Ni Ti and TiC
was obtained. The content of elements in the phas,4 A -Ni Ti
Card 1/2 was obtained from the difference after a second dissolution

Phase Analysis of Chromium-Fickel-Titanium Steels SOV/32-25-6-5/53
With Intermetallide Hardening
in the electrolyte 81 (50 ml KC1, 100 ml glycerin and 1050 ml
methanol) (Ref 2). Satiafactory results were also obtained
with the method TsNIIChM (Ref 3) (Table 1, results from both
method4 The electrolytic dissolution of the steel EI-696
heated for 100 hours over 8000v yielded titanium carbide and
-diboride and the intermetallide phases Fe 2Ti and K -Ni 3 Ti
at the anode (Table 2). A prolongation of the duration of
treatment of the anode precipitate with the electrolyte 81
showed no influence on the result of the X-ray structural ana-
lysis (Table 3) and the phases Fe Ti and tk-Ni Ti could not be
separated chemically. The steel BY-696 thus represents a six-
phase system: the hardening fundamental phase/5-Ni Ti, the
phases Fe 2Ti ando~-Ni3Tiq the two primary phases TiC and
TiB2, and the solid solution. There are I figure, tables
and 3 Soviet references.
Card 2/2

18(7) SOV/32-25-9-~10/53
AUTHORSt Blok,- No I,p* Kozlova, M*'Ne, Lashko, N. F., Sorokina, K. P.
TITLE: Boride Pha ses in Alloys on the Mokel _- Chromium Basis
PERIODICAL: Zavodskaya laboratoriya, 1959, Vol 25, Nr 9, pp 1059-1064 (USSR)
ABSTRACT: It was ascertained by experiment that the heat-resistivity of the
alloys (A) on nickel-chromium basis increases greatly with a
small content of boron. Metallographic investigations showed that
atO-01 - 0,5% of B9 eutectic deposits of the boride phase occur
at the grain boundaries. A method for the phase analysis of such
(A) was elaborated, in which the boride phases are,separated
electrolytically. The phases separated were subjected to X-ray
structural investigations and chemical analyses. N. M. Rudnevag
Ye. A. Vinogradoval and.K. V. Smirnova took part in the experi-
mental part of the work. (A) of the type E1473 (up to 0.23% B)
ast alloys ZhSZ (up to 0 22% B 11), E1617 (up to 0.5% B)
W,')c z ;
II , and the combined (A) h Z (IV Table 1) were used* Por
the quantitative separation of the boride phases the following
anhydrous electrolyte was the most suitable; 50 ml HC1 (1.19)t
Card 1/2 100 ml glycerin and 1050 ml methanol (Ref 2). Electrolysis took

Boride Phases in Alloys on the Nickel- Chromium Basis SOV/32-25-9-10/53
place for 60-90 minutes at a current density of 0.06 a/CM 2 under
ice-cooling. The chemical and X-ray structural analyses of the
anode precipitates showed (Table 2).that practically the entire
B occurs in the (A) as a compound. Besides, the boride phase,
titanium nitride was found in (I), and separated from chromium
boride (Table 3) according to the method (Ref 4). Formula
(Cr, Ni)5B4, or (Cr, Ni)4B3 oorresponds.approximately to the
boride phase (phase X) from (I)# which shows a tetragonal
crystalline structure. A combined boride.(phase Y) of the
incidental formula (MotCr,WNi) 4B39 or (MovCr,WqNi)5B4 is formed
by an increase of the borium. content in (II), (III), and (IV).
The crystalline structure of this phase could not be ascertained.
It is assumed that this phase is a ternary, or more complicated
compound. Data of X-ray structural analysis according to the
powder method for the two phases X and Y are given (Table 4).
There are 2 figures, 4 tables, and 3 references, 2 of which are
Soviet.
Card 2/2

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PHASE I BOOK EXPLOITATION SOV/4270
Lasbko,, Nikolay Fedorovich,, and Soflya Vas:Lllyevna Lashko-Avakyan
Svarivayemyye legkiye splavy (Weldable Light-Metal Alloys) Leningrad., Sudpromgiz,
1960. 439 p, Errata slip inserted. 3.,400 copies printed.
Scientific Ed.: G.L. Petrov; Ed.: Yu. S. Kazarov; Tech. Ed.: R.K. Taal.
PURPOSE: The book is intended for scientific and technical personnel engaged in
research, development, and use of weldable light-metal alloys.
COVERAGE: The book contains results of investigations of the structure of welded
joints and the causes and prevention of hot cracking. Basic characteristics are
given of industrial alloys and recently developed aluminum-, magnesium-, and
titanium-base alloys. An analysis of the weldability of these all ys is also
presented. Conditions for making high-grade welds are discussed. No persona.3-i-
ties are mentioned. References accompany each part.

S/593/60/000/000/005/007
D204/D302
'AUTHORS: Blokp N.I-p and 1ashko,_N,LZ_!
TITLE; Phase analysis of certain multicomponent alloys t!j
SOURCE: Soveshchaniye po khimicheskomu kontrolyu proizvodstva v
metallurgicheskoy i metalloobrabatyvayushchey promyshlen-
nosti. Dnepropetrovskq 1958* Yhimicheskiy kontroll proiz-
vodstva i metallurgicheskoy i metalloobrabatyvayushchey
promyshlennosti; [doklady Boveshchaniyaj ODnepropetroveli]
.1960, 246 - 250
TEXT: A description of phase analysis of a number of refractory al-
loys based on Ni-Crf among them 3H-437 (EI-437), Ei-617t )YC3
(ZhS3), EI-698p BI-598 and BI-765, The highly dispersed al-phase
was separated electrolytically, using electrolyte no. 18 (10 g
.(NH 4)2 so 4t 10 g citric acid, 1200 ml H20); the carbide and boride
phases with electrolyte 81 (50 ml conc. HOlt 10 ml glycerine, 1050
mi methanol).& Chemicalf X-ray and metallographic methods were used
to-study--the composition, structure and extent of the various pha-
.Card 1/2

0 67861
SOV125-60-1-4/18
AUTHOR: Lashko-Avakyan, S.V. and,,LaahkQ_N.,F. (Moscow)
TITLE: Crystallization Cracks Near Weld Seams
PERIODICAL: Avtomaticheskaya svarka, 1960, Nr 1, pp 27-37
(USSR)
1~
ABSTRACT: The peculiarities and probable processes of crack
formation near weld seams, mainly in aluminum alloys, _~i
are dis sed. Data from existing wor_k_s /Ref 1-9/ as
well as experimental evidence are presented in support
of the inferences drawn. Macro and microphotographs
of seams in steel and aluminum alloys are given. The
nature of near-weld crystallization cracks is attri-
buted-to the formation (not growth) processes of metal
grains, observed experimentally with the VIM-lM micro-
scope, in the base metal at the seam. It is concluded
that the tendency to form cracks can be diminished by
rapid heating of the base metal to melting point, by
Card 1/2 producing a small zone of partial melting, and by any

67861
SOV/125-60-1-4/18
Crystallization Cracks Near Weld Seams
means conducive to the formation of a fine grain
structure in the base metal near the weld. The
following filler metals prevent cracking in and near
the weld during the weldiAg of duraluminum: 11AK111%(4.5-
6YO Sii the test aluminut) Cu: 2-:T-.50lo Ni;
1.2-1.6% Mg; 0.4% Mn; 0.25--.35% Ti; the rest aluminum).
These filler metals form more easily fusible alloys in
the seams. There are 7 photographs, 4 graphs and 9 re-
ferences, of which 8 are Soviet and 1 English.
SUBMITTED: July 2, 1959
Card 2/2

S/135/60/000/005/003/009
A115/AO29
AUIHORS: Popova. L.S., Engineer; Lagg&,_ Candida+e of Technical Snien
ces
TITLE: Hardening in the Heat-Influenced Welding Zone of Struc;tural Marten-
site Steels
PERIODICAL: Svarochnoye proizvodstvo, 1960, No~ 5, PP. 11 - 15
TM: The structural martensite steels 11 are processed for 150 k&/mm2.
Immediately after welding,\qthe solidity limits of weldments decrease to 50 - 75%.
In -the zone of thermal influence of a weldment a section is found In which -!,lie
process of disintegration Is caused by destruction of martensite substance, i.e..
of oversaturated alloying elements and by coagulation of carbide phases. The
location of the destructed part depends ci, tbe method of welding. ~n structural
martensite steels, a carbide'~Jhase of the type of cementite Me3 is formed con-
taining Mn, Cr, Mo, W, V, Ti and Nb. The ra-~e of cementite coagulation depends
-ion of the alloying elements between the solid
on the possibility of distribut
solution and the Isolation phases. Therefore, the rate of cement'-te growth is
higher with chrome steels than with, molybdenum or vanadium steels. Higher
Card 1/3

S/135/60/000/005/003/009
A115/AO29
Hardening in the Heat-Influenced Welding Zone of Structural Martensite Steels
strength in the zone of thermal influence can be achieved by alloying the steel
with Me7C3, Me2C, MaC and Me23C6. The best effect of strengthening steel by
the cementite phase Me3C can be obtained at 100 - 3000C depending on the alloy-
ing elements. The best strength of structural. martensite eteels i's retaired
with Me7C3 carbides at temperatures of up to 5000C depending on alloys and ther-
mal treatment or by carbides Me2C or MeC aT. 500 - 6500C. To Investigate tne
disintegration of solid solutions in the zone of thermal Influence of welding
tvio''5'~ri*e_s'_of alloyed steels containing 0.20 0.30% C have been used (Table 1).
In the'first series (No. 278N, 320, 464), depending on chemical composition,
one-phase disintegration with subsequent formation of Me3C and corresponding
carbide phases Or, F07C3; W2C', VC was obtained and In the second series of
steels (No. 265., M, 277_~ 187, 278), depending on chemical composition and t.h., e
zone of thermal infl:uerice., one-phase, two-ph-a_=--_ and three-phase disintegration
of the solid solution has been produCed. The average content. of alloying ele-
ments is 0.25% C, 2% Or, 1% W, 1% Ni-Ir 0.25% -,fa. Steels were smelted in an in-
duction furnase. and one of the alloying elements-, C, Or., W.. V was added. The
bars were pressed to 4--mm plates., heated to 8900C., --ooled in oil for 15 min wit"
C ard ~V3

S/135/60/0()0/005/003/009
4115/AO29
Hardening in the Heat-Influenced Welding Zone of Structural Martensite Steels
subsequent tempering at 2000C for 1 hour; are-welded manually with 90H~i-13/85
(UONI-13/85) electrodes. Results of mechanical tests of weldments and basic
metal are given in Tables 2 and 3. Tables 4 and 5 show results of chemical and
X-ray inspections. The smallest increase in firmness after two-phase treatmens
has been noted in the cases, where only vanadium was used as alloying substance
(solution No. 464). A considerable part of vanadium is bound In the form of
primary vanadium carbides VC. These do not dissolve, even If heated up to,
1,3000C and do not participate in strengthening the steel. VanadiLumjbinds a
large part of carbon and the share of martensite strengthening is decreasi1g. In
steels alloyed with tungsten the solidity of weldments increased from 64 to 83.3
kg/mm2. in case of chrome, the solidity of weldments was strengthened up to
8o - 85 kg/mm2. Significant Improvements were achieved at welding steels alloyed
with tungsten and chromium - (100 - 105 kg/mm2). There are 5 Soviet references,
J-1
Card 3/3

21392
S/032/61/027/012/002/015
B119/B147
AUTHORS: Blok, N. I., Glazova, A. I., Lashko, N. F., Kurayeva, V. P.
Molchanova, Ye. K.
TITLE: Phase analysis of alloys on titanium basis
PERIODICAL: Zavodskaya laboratoriya, v. 27, no. 12, 1961, 1470 - 1472
TEXT- a+p-alloys with stabilized P-phase, and a-alloys with intermetallic
hardening were examined. The individual phases were isolated by anodic
solution of the alloy in anhydrous electrolyte (3 g of KCNS or 2 g of
LiCl, 10 g of citric acid, and 1200 milliliters of methanol). There-
after, they were subjected to X-ray structural and chemical analysis.
Ab,V,Nb,and Ta were identified as stabilizers for the P-phase, the effect
of which decreases in the sequence mentioned (In the presence of 4% Mo
the content of the P-phase in the alloy is 1;%; at 4% V, it is 9%, and
at 4% Nb or Ta, only 3%). After forging, the anodic deposit of these
alloys consists entirely of P-phase. In the presence of 4% Ta, alloys
aged for 100 hr at 500 0C show only small quantities of P-phase, whereas
45 Mo or V completely prevent the P-phase from decomposing. Ti-Cu
all oys containing up to 5% Cu have one phase of the composition Ti 3 Cu
Card 1/2

Phase analysis of alloys on ...
21392
S/032/61/027/012/002/015
B119/B147
with tetragonal face-centered lattice. A phase of the type Ti 3Cu of
different composition was also observed in Ti-Al-Cu-Sn alloys (containing
up to 3-5% Cu). An increase of the Cu content of these alloys from
2 to 3.5% results in a rise of the content of (TiA1,Sn) Cu phase from
3
5.75 - 6,25 to 8.02 - 8.34%. Thus, strength increases from 95 - 100 to
104 - 110 kg/mm2. In this case, specific elongation decreases from 35
to 30 - 22%. Ye. A. Vinogradova, Ye. V. Zvontsova, and L. V. Polyakova
assisted in the experiments. There are 1 figure, 3 tables, and 5
references: 2 Soviet and 3 non-Soviet. The two references to English-
language publications read as follows; N. Karlsson, J. of the Institute
of Metals, 79, 391 (1951); A. Gaukainen, N. J. Grant, C. F. Floe, J. of
Metals, 4, no 7, 766 (1952).
Card 212

B/133/60/000/007/011/016
AUTHORSt ~ashko, N.F.; Popova, N.M.
TITLE: The Distribution of Molybdenu and Tungste in the Solid Solu-
tion and the Carbide Phases of Alloy Steels
PERIODICAL: Stall, 1960, No. 7, pp. 642 - 644
TEXTs Tests were carried out toreplace molybdenum by tungsten in
ther&ostable and heat resistant steelsV The present paper discusses the
problems of inclination of molybdenum and tungsten to concentrate in car- V/
bide phases formed upon the decomposition of the solid solution in heat re-_
sistant steels. Steels containing the most frequently occuring carbides
C 1 Me`~ ) were examined. The low-alloy steels were e-
(Me3C, MeC, Me23 6, Men, mC
lectrolyzed in a potassium chloride and citric acid solution cooled to OOC;
steels with a high chromium content were treated with hydrochloric acid ad-
ding sodiumthiosulfate (Ref. 5), nickel alloys in a solution of hydrochloric
acid and sodium fluoride. The dissolution was carried out during 4 hours
at a low current density (max. 0.02 amp/CM2), the anode deposits wbre washed
with water and an alkaline solution in order to eliminate the amorphous re-
sidnes of tungBtic acid and molybdenum BulfideB formed during the electrol-
Card 1/2

S11331601000100710111016
The Distribution of Molybdenum and Tungsten in the Solid Solution and the
Carbide Phases of Alloy Steels
ysia and other impurities. Six types Of steels were tested and mainly the
carbides of type Me3C, which form in the steels A(A), G(B) and B(V), were
examined for Fe, Or, Mo, W and V content, after hardening at 1,0500C.and
tempering at 3500C, 4000C and 4500C with holding times of 50 and 200 hours.
Under all conditions of heat treatment At was found that the relation of a-
tomic contentsD[ola 9 [W],,, *as higher in the Me3C carbide than in the in-
vestigated A, B and V steels and from this it was concluded that molybde-
num is a more powerful carbide-forming element"Ithan tungsten. This can be
explained mainly by the relatively smaller atomic radius of.molybdenum. pro-
moting its diffusion in steel. As the increase in molybdenum and tungsten
concentration is accompanied by an increase in the thermostability of the
carbides, this also bringsabout the increse in thermostability of the
steel. Similar conclusions were drawn from other steels examined. There
are 5 tables and 6 references; 5 Soviet and 1 English.
Card 2/2

AUTHORS: Yelagina, L.A., Lashko, N. F.
S/762/61/000/000/005/029
TIT.LE: Decomposition of the A phase in alloys of the titanium- chromium-
aluminum system containing 7% (Cr+Al).
SOURC4.-,'- Titan v promyshlennosti; sbornik statey. Ed. by S.G.Gla7,unov.
Uoscow, 1961, 79-84.
TEXT; the experimental investigation reported in this paper was performed to
study the process of the aging decomposition of the metastable solid-solution (SS)
phase formed by quenching a Ti alloy with 77o Cr and to clarify the nature of their
hardening and the reason for the brittleness evoked by the accompanying formation
of a metastable w phase. The alloys were prepared from sponge Ti TiDO, Al AOO,
and electrolytical chromium. 3-kg ingots, 120-mm diam, were cast (chemical
compositions tabulated). Test rods 14x 14 mm were forged at 950-11500C (depen d-
ing on composition) and cut into test specimens 20-25 mm long. Tests were made
for H ' microstructure, and phase composition of the alloys in three states:
,(a) AZer 2-hr tempering at 6500 and cooling in the furnace; (b) after water quench
from 1,0000 (30 min); (c) after quench per (b) and 4500 aging with various soaking
times (according to P. D. Frost, et al., Trans. ASM, v. 46, 1954, 23 1). Tempering
at 4500 with aging yields maximum hardening with a Ti-7.5Cr alloy. Tempering
.increases the Hv with increasing Al and decreasing Cr content. Quenching increases
the hardness of alloys with 7-2loCr and 0-57oAl. does not affect that of the Ti- lCr-
Card I /Z