SCIENTIFIC ABSTRACT KRISHTAL, L.I. - KRISHTAL, M.A.

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• Collection: Scientific Abstracts
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• Sequence Number: 15
• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTRACT

TRUBIKMV, H.C., kmd. ekenom. nauk; FlSY'-,HM.Vl, kand. ekoncm. nauk;
KREYNZ, A.V.7 kand. 6k'7'T;')m. nwak., 1.91*1 red*
(itincilPco f,~r the emtAj.'a'ne7,.t of r:illrcad rreight rates In
n.-.,clalLit irbi,?igament). ?i-Intsipy postroentiA zheleznodo,-Pozbnykh
gruzco,v-ykh tarlfu7 -T rol.l~nlisti:,bel;kcm. khrzististve. Moskva,
Transport, 46 p. ixnyl naucbno-iseledoystell-
skil Institul. zbeleznod.-.rnzt:rrE- trinsporta, Trudy, no.278),
(MIRA 17r)

VINOGRADOV, A.N.; LIVSHIN, G.L.; OLHAZTSOVA, R.I.; TULUPOV, L.P.;
Prinimali uchastiye: RAZORENUVA, L.K... inzh.; J)-UBINKINA,
L.I., inzh.; PODGORNYKH, A.L., inzh.; IAVRENTIYEV, N.V,s
retsenzentj MINAKOV, A.D., retsenzent; NESTEROV, Ye.P.,
retsenzentj STEFANOV, N.Ya.j reteenzent; USHAKCFV, P.S.j
retsenzent; L.I., red.; KHITROVA, N.A., tekhn.
red.
(Calculating machines in accountings planning and administra-
tion in railroad transportation) Vychisliteltnaia takhnika v
uchate, planirovanii i upravlenii na zheleznodorozhnom, trans-
porte. (By] A.N.Vinogradov i dr. Moskva, Tranazheldorizdats
1963. 407 P. (MIRA 17:2)

BERLYA14D, A.U., otv. za vyprusk; KRISHTALIj LI.j, red.;
VOROTNIKOVAO L.F.p tekhn. rW-.
[Collection of materials on traffic safety; excerpts from
orders and instructions issued by the Ministry of Railroad
Transportation on traffic safety] Sbornik materialov po
bei,opasnosti dvizheniia; vyderzhki iz prikazov i ukazanii
Ministeretva putei soobshchenlia po bazopaanosti dvizheniia.
Izd.2. Moskva, Trang2heldorizdat, 1963. 206 p.
(MIRA 17:2)
1. Russia (1923- U,S,S.R,) Upravleniye glavnogo revizora po
bezopasnosti. dvizhenlya. 2, Starshiy pomoshchnik glavnogo re-
vizora po bezopasnosti dvizheniya Ministerstva putey soobshche-
niya SSSR (for Berlyand).

FErROV, Vaevolod Ivanovichp kand. tekhn. nauk; alSHTALI, L.I.p
red. - I --,
[Transportation and economic ties of 'the U.S.S.R.J Transportno-
ekonomicho8kie Bviazi V>SRI abornik atatel. Moskvaq TranBportg
1965. 170 p. 18:4)
1. Moscow. Institut kompleksrqkh transportrVkh problem.

ZAKHAMKO, Nikolay Nikolayevicbj 1111411, Ley Mendeleyevichl
KRISJUAL' , L.I.,, red.
[Ways to increase labor productivity in rallroad
transportation] Puti povyshenila proizvoditellnosti
truda-Y khozielotye dvizhenlia. Mookvaj Transport#
.1964. 151 Pe (MIRA 17:12)

L -__
1:CjN'01,'AIa',V, Sorgey Alekvan,tr~jvichj j4dSH-T~iL.' V I.. t. y -(;d.
(Long-term planning of suburban passorwer trantport&-
tionj in the eactiun and on the railroad an a whole)
Ferspakti,moo planirovanle prigorodnykh perevozok pas-
sazbirov; na. otdelenii i zheleznoi doroga. MomWit,
Transport, 1964. 34 p, (Miftill IIli)

VLADIMIROV, V.A.1 KRISHTALI, L.I., red.
[Original statistical accounting on rallroada) Per-
vichzWi statiaticheskil, uchet na zheleznykh dorogakh.
Moskvap Izd-vo *Transport," 1964. 57 p.
(MIRA 170)

I'1Z'Cj"AkEV, Scrgny Aleki3aMrovich; MISHTALI, L.1., red.
(Loi4l-turm planning of suWiL,,;n puisonger transportation;
on railroad lines and sectious) PerspektivnoO Flnnirova-
niu 1)rifrorodnykh perevazok passazhirov; rui otdolanii i zho-
leznoi doroge. 14oskva, "Transport," 1964. 34 1).
(MBU 17:F)

01:AiTALf, L.1s, rod.
[Establishing -the norms for industrJal supylion of materialB
and Bpare parts in locomotive and car deFots; methodological
manual) Normirovanie proizvodstvennykh zapasov materialov i
zapasnykii chastei v lokamotiviWkh i vagor-Mkli depo; metedi-
cheskoe posobie. Moakvaj Trawnport, 1964. 29 p.
WIFU 17:8)
1. Moscow. Vsesoyuzrrjy nauchno-issledovatellsidy institut zhe-
leznodorozImogo -transporta.

FETROKANSKIY, B.I.; ZVEREV, N.P., retsenzent; MIZIN, V.I.,
retsenzentj PEIROV, A.I., retsenzentj Mj=--AL1, L.I., red,
(statistical accounting and the work analysis of a railroad
branch] Statisticheskii. uchet i analiz raboty otdeleniia do-
, rogi. Moskvap Izd-vo "Transport," 1964. 218 p. (MIRA 17:5)

IVLnVo, I.V.; PETRUKMIOVSKIY, I.V.',*retsenzent,-j KRIMNUS, G.Kh.
Iretsenzent'; NAUMOVI G.I.'reteenzent ORLOVI V.N.
.retconzent 1 TUCHKEVICH, T.M. retaetzent USHAKOVpP.S.
,reteenzent ; CHERNUKHAj N.T. retsenzent EDELISHTEYN.
P.G. retsenzent,;,PISHTALO, L.I.p red.; VINNICHENKQ,,_N.G.,
kand. ekon. naukp red.; USMKO, L.A., tekhn.red.
(Finance and the financing of railroad transportation]Fi-
nansy i finansirovanie zheleznodorozhnogo transporta. Mo-
skvas Transzheldorizdntj 1963. 439 p. (HIRA 17s2)

PETROKANSKIYO B.I.j ZVEREVp N.P.j, retsenzenti MUM, V.1.0 A
reteenzentj PETROV, A.Lp retsenzentj KRISHTAL'I.LsIsp..,
red.; MURAVIYEVA, N.D.p takhn.red. ~_ _-_'
'dr
(Statistical accounting and the vork analysis of a rail-
road division) Statisticheskii uchet i analiz raboty ot-
delenlia dorogi. Moskva, Izd-vo "Transport w 1964. 218 p.
WRA 17:3)

- -- - - - TAOROT - - L-8 - -~-- INSHMO - L. 1. - DKITRIYET. V.A.
I a 60
--- --momoom
[Pri4olples of railroad statistical Olno sholesnodoroahnoi statiatiki,
[Rodakiory Kriebtall. L.I.. Dwitriev, V.2 Koskva# goo, trausp, shol-dors
lvd-vo, 1953. 194 p, (KLU ?tl)
(pailroado-Statieties)

LUGOVOY, P.A., inzh.; TSYPIN, L.G., inzh.; GIBSHW, A.Ye., prof.,
doktor tekhn. naukv retsenzent; USHAKOV, S.S., doktor
tekhn. naukp retsenzent; KA15HTALI,_~J., red.;
VOROTNIKOVA, L.F., tekhn. red.
(Technical and economic calculations in the reorganiza-
tion of railroads) Tekhniko-ekonomicheskie reschety pri
re onstruktaii zhelesnykh dorog. Moskva, Trans sheldorisdatt
1963. 246 P. (Nin 16:4)
(Railroad engineering)

KAPLANI A.B.; NESTEROV, Ye.P., retsenzent; KRISHTALI, L.I., red.;
DRDZDOVA, N.D., takhn. red. " - , 1.1-- -,
(Cybernetics in railroad transportation) Kibernetika
na zheleznodoroshnom transporte. Moakva, Tranazheldor-
izdat, 1963. 66 p. (MIRA 16:11)
(Railroads--Electmnic equipment)
(Railroads-44anagement)

TISHCHENKO, And~ey Ignatlyevioh; SAMOKHVALOVp V.A., retnenzenti
KRISHTALI, L.I., red,; VDBDTNIKOVA, L.P., tekhn. red.
[Technological rodrpnization of traction] Tekhnicheskaia
rekonatruktaiia tiagi. Moskva, Tranesheldorizdat, 1963.
131 P. (Locomotives) (Railroads-Menagment) (MIRA 16:7)

ISTOMIN, L.I.; SHUBNIKOVp A.K.; POPOVI V.M.; MOLYARCHUX, V.S.,
reteenzent; PAISHIKOV, V.A., retsenzonti KRISHTALI, L.I.,_
red.; KIIITROV, P.A., tekhn. red.
(Unear programm~~'-in the planning of Ihe'&el and
electric-power supply for railroad transportation] Linei-
nos programmirovanie v planirovanii toplivo- i energoanab-
zheniia zheleznodoroahnogo transporta. Moskva, Transshel-
dorizdat, 1963. 178 p. (MIRA 16:10)
(Lineir programming) (Railroads--Management)

MIKHKYEV, A.F., doktor tekhn, nauk, prof., red.; Yj-,.!S.HTAL', L:.'.,
red.
[Banic trends in the develorant of transportation tech-
nology in foreign countrlosj Oanovnye napravlenila v ra7,-
vitii tekhnlki tranaporta za rubezhom. Moskva, Transport,
1965. 335 p. (MI RA 16: 4)
1. Moscow. Institut koml)leksnykh transportnykh problem.

---- - -- --- --l-
Ned of lUkft Do the VqWdubm of P. -
nil"itl an $k Met. Inst.).
Votmat '~~M ft'llal-l= X171,950. 213-7 -A
i Murrov Sefshus

A15~1 5#71qz , M ~ 4 -
KIRSTUL, M. A.
USSR/Ifttals - Cost Lron, Proceises NOT 51
"Concerning Graphitization of White Cast iron,"
M. A. Kirshtal
"Litey Proizvod" No 11, YP 31, 32
Presents exptl evidence of'shlfting of iron atoms
In process of decarburization of graphitized cast
irons. Results obtained permitted study of effect
of Sicontent, on rate of decarburizing, process and'
detn or activation enbr& of this proc*bss.' * Considets
graphitization as process reverse to decarburizatibn
of,graphitized cast iron and explains accelerating
effect of silicon on gral-bititation-process6.

IRISHTAL. N.A.
--------
Thew of graphitization of white Iron and steel.
Jo 153.
(Iron-Metallurg
.y)
Lit.proisv. no.6:22-24
(VIA1 6:7)
(Steel--Metallurgy)

US S R
~v termmatioz *f the alor oaM o
':a (m co' clct=LAL
liat:nita %nd in Itmts
L17&-W~tllml -A
ptx~ 11
,!~tn tA coefft
Fc-~ tf~ rhis fzl,tlt~i - be .,.ei q
vil, ~,l -lt-o, T'L,: f lhe 110u- -11 J
vqM t~v, Ual tucthod at Qjttr -~J~

.1 1 . I
: . .":
! : :.. -- " f 1
- a , ,- F

g1rhilec"Idtaks, and the C cemlent was ticid a: 4.0~. Thc
6
4 CM(rut was vmtw betwe" I and 5%. 5hecto 1003 mm.
thick Were cast continuouxik, CPA wem heid at
- In pwr It The digusioe L~*h. a( C was dnd bv 0tv ~rlm-
tty wfth which &Q auitenitic ed4e wj" famied The cunrcs
thnw that sharp drnln in the diffusim mtc ~e
at I uld 4% ca;` Mewurewat (d t1cc. PC,(-cntws 4 tht
tflo~% *VdpjeArmoo Ims Uspd (CIC Omt . to a 0.01 ill
rwtpn
I(.SO.s(u;vkdtw-fmim.. mpfoat I and t% Ca. Itsprcars
that Co (cwm* a ItATT at, "ling with kicaltrC4 electmn
tgtmdt, SWIM the C diffti4w procru takcs pLacv m aul-
(Cr4ce, PmAoW moo a$ the C* k perwAt to this phtee. a"
VAlf ocue

/T f-
M/ Engineering - Technical physics
-Coxd 1/1- j-Pub.-22 - 19/49
Authow i Krishtal, H. A.
TMA I Fast graphitization of white cast-irons having a higher content of
chromium
Perlodleal I Dok. AN SSSR 98/4, 583-584, Oct. 1, 1954
Abatnwt A method which helps to speed-up the graphitization of white cast-iron
(caat-iron with a high % of chromium) is described. Five references
(1945-1953). Graph.
Institution Arkhangelsk Foreit Institute
Presented byiAcademician G* V. Kurdyumov, April 24, 1954

ULSII/ :,.nFj1r,eerinF. - lechnoloa
Card 1/1 Pub. 22 - 26/0
Authors I Krishtal, M.A.
Title I The.nature of a process affecting the speed of cAst Iron graphMtALion
Periodical I Dok. AN.SSSR 99/6, 983-986, Dec 21, 1954
Abstract I Experiments, intended to determine the nature of a process which reduces
the speed of cant iron graphitization, are described. There are two con-
cepts with regard to the speed of cast iron graphitization: one is based
on the idea of carbon diffusion and of iron self-diffusion. The other is
based on the idea of the speed of the removal of iron atoms from the cast
iron as the graphite content uvrows. The expariments were conducted to de-
termine which process is the more acceptable. Twelve USSR referencei
(19.0-195J). Graphs.
Institution: 1he Archangels% Forevt,Technical Institute
Pregented by: Academician sk.N. 'k,erenin, Aupst 6, 1954

KRISHTAL, 1-1. A.
Krishtal, H. A. -- Me Effect of Alloying Elements on the Kinetics and
Mechanism of Graphitization of White Cast Iron." Min Higher Mucation USSR.
Moscow Order of Labor Red Banner Inst of Steel imeni I. V. Stalin. Moscow,
1955. (Disseration For the Degree of Doctor in Teelmical Sciences).
So: Knizhnaya Letopis', No. 11, 1956, Pp 103-114

., .:I- --
":*T11 . - 1 1-4- -, -
i-,P ~r .

KRISHTAL.M.A.
The graphitization theory. Idt.proixy. no.9:30-31 5155.
(Cast iron--Metallurgy) (KLRA 8:12)

metheid for deurmWal, the cotfficfert of sell dirusioa ut
trol ba a.1107a4 austenits. 14, A. Kriexzl~ Zhu? r#AA 'I
Figi 2.5, , I '~Ccked ""bacro
If cc ~ Wo! A tioli-
tak-~ii place hy tneans of h.711 ".,N
prr---13E in a arytial trial bc filled wlt.~ &n ~djrfatmc tC1V
=--sing it 19 mo-m for onc interat. sprice. A dL4:A#L,,!!1-nf
,f t ho!, (oz R enmLdtrable dittmixct do- u, t
,-c-- r
-uf;nC itio,,tnitnt of an atom A (J a rt ~f
one hitetat. vtweschic-s the itt-It. Yhrtr
Is Ito 11"d for an atom to travizf frrn the t,Yrf4i:,! Intn 1he
~.~y oi nietall lor Mline inte.triml Attnt:i of Fe diFuso
In th!s timinct, as cao tic gecn In cra gilt i tiratifm I,oles
must truvel to graphite inclusions to lxrinit C atx-.-.s to join
the latter. Diff4sion promr-S have (tic VLICX-ity thi,, 40!ci
travial, an4 the decatirbufrization resetints off 0-5-miu, .1
varthilic imn in Ift, was "%cd foc it& d-cotonmration. kito'-
ari-ig the thirknesti of noisicnitic layer firce fmn emplitte a, a
iwnrficrn of timi, gives this Velocity Sprcinl~-~Cnnte 41-14~
C xpd 0.6, 0 9, 1.2% Si and thogc i;h tfl~e ~me C and 1.
2.5, and M7, Ki wen decarbudreti at giving the
" e( sell diffusion of Iran. Atll)20'theiflffusionvel~~i-
"Cfthc Si &!Tties Screg.1 X 10-0. 1.05 x 10-, an4 1.8-4 x
10-", while M incremsed it to 2.32, 9-Z3, and 14.0 X 10-.
This diflusion veloicity Is a!mut 4 orders of ma&mittld eoW
tabu , 'T
ttu" t,vkt of pore (tom. D!1U%i= dAtii. am is .
J. D. GAL-..m

IRA,;
?

R-0
Ell
OWN,

AUTHOR: Krishtal, M.A., Eng. 129 - 8 -5/16
TITLE: Influence of preliminary hardening on the diffusion speed
of carbon in the austenite. (Vliyaniye predvaritellnoy
zakalki na skorost' diffuzii ugleroda v austenite).
FMIODICAL:"Metallovedeniye i Obrabotka Metallov"(Metallurgy and
Metal Treatment), 1957, No-8, Pp.20-21 (U.S.S.R.)
ABSTRACT: During heat treatment steel components may be subjected
to repeated hardening and, therefore, it is of interest
to study the influence of hardening on the speed of diffusion
of carbon in the austenite. This was done by means of a
metallographic method based on studying the speed of
decarburisation of white iron described in earlier papers
of the author (3,4). As test specimens the authors used
0.5 mm thick white iron plates containing 0.4% Cr and about
4% C; the material was produced by "liquid rolling" of melts
smelted from commercially pure iron. The specimens were
decarburised in a hydrogen stream at 850 C during one-and-a-
half hours and as a result of this an 0.120 mm thick
austenite layer was obtained with a carbon concentration
approaching zero at the surface. The results are summarised
in a table and a graph which gives the influence of the
umber of hardening operations on the value of the coefficient
Card 1~12

Influence of preliminary hardening on the diffusion speed
of carbon in the austenite. (Cont.) 129 - 8 - 5/16
of diffusion of carbon in the austenite. It ~:an be seen from
this figure that-with increasing number of hardening operat-
ions the diffusion of carbon in the austenite decreases.
there are two figures, 1 table and 5 references, 4 of which
Are Slavic.
ASSOCIATION: Tulsk Mechanical Institute (Tullsk.iy Mekhanicheskiy
Institut).
AVATLA LE:
Card 2/2

AUTHOR: Krishtal M A SOY/163-58-1-37/53
TITLE: On the Mechanism of the Diffusions in Volume Centered Iron
(0 mekhanizme diffuzii v obl'yemnotseritrirovannom zheleze)
PERIODICAL: Nauchnyye doklady vyashey shkoly. Metallurgiya, 1958, Nr 11
pp 201-205 (USSR)
ABSTRACT: Iron and many iron alloys have volume centered lattices and
therefore are of great importance in the explanation of the
mechanism of the diffusion in a- and 6-iron.
To explain the pore formation in volume centered iron samples
were annealed at temperatures where 8-Fe occurs.
All samples investigated by metallographic analyses and micro-
photographs prove that none of the samples was without 'Pores.
In microphotographs pores of uniform shape are present. The
presence of pores in iron is proved by the diffusion of iron
and tantalum in volume centered iron alloys. The shape of
pores occurring most frequently is pentagonal.
By means of the microphotographs the depth of the penetration
of the tantalum atoms into iron was determined. The mean
magnitude of thin penetration is 0,256 mm.
Card 1/2 The magnitude of the diffusion coefficients of tantalum in iron

SOV/163-58-1-37/53
On the Mechanism of the Diffusions in Volume Centered Iron
2
may be oalculated by the following formula: D !-, where x
4-r
denotes the depth of penetration and i the duration of the
treatment of the sample at 14500C. -8
The diffusion coefficient has the order of magnitude of 10 -
'0 -9 cm 2/sec.
I
There are 5 figures, 1 table, and 6 references, 4 of which are
Soviet.
ASSOCIATION: Tul'skiy mekhanicheskiy institut (Tula Mechanical Instit,ite)
SUBMITTED: October 1, 1957
Card 2/2

'00"'t/
AUTHORt Krishtalp II.A., Candidate of Technical Sciences 128-58-5-10/16
TITLE: Calculating the Limiting Factor of the Graphitization Process
(K raschdtu limitiruyushchego faktora protsessa grafitizataii)
PERIODICAL3 Liteynoys Proizvodstvot 1958p Br 5t pp 22-24 (USSR)
ABSTRACTs The author lists the different points of view on the factors
limiting the aphitization process in malleable cast iron
-
Ilef. 1 - 1 and analyzes the formulas suggested by different
f
authors for determining the diameter of the growing graphite
inclusions as a function of time, for determining the activa-
tion energy, eto. He comes to the conclusion that the speed
of the initial graphitization process in Fo-C-Si alloys is
controlled by the speed of the vacancies in austenite toward
the growing graphite inclusions. He points out, however, that
this conclusion can only be accepted as yet for the case of
Fe-C-Si alloys of studied concentrations. In other cast irons,
and particularly in alloyed cast irons, the graphitization
process can be controlled also - as was already indicated - by
the speed of the plastic flow of mold, by the diffusion of
Card 1/2 carbon, and by the solution of carbides.

Calculating the Limiting Factor of the Graphitization Process 128-58-5-10/16
There are 13 referenceep 9 of which are Soviet and 4 Engllohs
AVAILABLEt library of Congress
Card 2/2

:;0V- 128 - _z 8 -
AUTHORS: Kr' Y,A., Candidate of Technical S~;ienses, Fcm~nykh,
.:t.9 ~tl
of Technical Sciences, Rikman, E-P
,P., Cqndida , Engineer
TITLE: Peculiarities of Magnesium Distribution During Annealing
of Magnesium-Treated Malleable Iron (n3obennosti. rasprede-
leniya magniya pri otzhige
PERIODICALt Liteynoye proizvodstvo, 1958, Nr 8, pp 10-11 tUSSR)
ABSTRACT: The effect of magnesium on the formation of spheroidal gra-
phite has been studied since the discovery of magnesium iron
ZR-ef,1-17. The purpose was to study the behaviour of man-
ganese in the process of annealing, e,g. the redistribution
of magneaium between the metal and the graphite. The study
was carried out on specimens of iron of different composi-
tion and with the use of a device fcr localized spectrum
analysis (described and il2us-.rated b * a diagram), It was
stated that silicon, solved in MeVil, tie3 iragne3ium, and
hence an increased silioon content in iron entails an 'Ln-
creased solubility of the manganese therein. The bond be-
tween the atoms of silicon and magnesium impedes the trans-
fer of magnesium from the matrix (austenite) into the gra-
Card 1/2 phite during the process of annealing. In low-silicon iron,

Peculiarities of Magnesium Distribution During Annealing of lliagnosium-
Treated Malleable Iron
the magnesium atoms in the matrix are only weakly bound,
and migrate into the graphits even at comparatively low
temperatures. There are 2 graphs, 1. diagram, and 7 refer-
ences, 5 of which Are Soviet, 1 Engl,--Qh 9-ni I German..
I. iron alloys--Heat treatyrint .2. effects
Card 212

vo
Ila jv- fill
vial 'Veil
IN
411
If %a
. I . I. i
,ua " a
"Pi

18 (7)
AUTHORS t Krishtal, MO Golovint S. A, SOV/163-59-2-30/48
TITLE: The Relative Fading of Torsional Oscillations in the Thermally
Treated Steels 50A and VA (otnocitellnoya zatukhaniye
krutillnykh kolebaniy v termicheoki obrabotannykh etalyakh
50A i U7A)
PERIODICAL3 Nauchnyye doklady vysshey shkoly. Metallurgiya, 1959,
Nr 2, pp 173-175 (USSR)
ABSTRACT: The authors investigate the internal microplastic friction in
the hardened and drawn stools mentioned in the title in order
to clarify the connection between metal structure and internal
friction in carbon steels. Products of these sorts of steel
(springs) are exposed to rapidly changing loads. The composition
of the two steel types is indicated in a table. The internal
microplastic friction was determined by the fading of the free
torsional oscillations which were recorded by a special
apparatus with tensometrio recording of the vibrogram. The
results for the two steel types are represented in figures 1
and 2. They show the dependence of the torsional oscillations
on the voltage applied to the periphery of the sample. rigures
Card 1/2 3 and 4 show the influence of various drawing temperatures.

The Relative Fading of Torsional Osoillations*in the SOT/163-59-2-30/48
Thermally Treated Steels 50A and 17A
At drawing temperatures between 450 and 5500p a considerable
reduction of fading occurs. It in explained by-& splintering
of the blacks of the cL-phase in drawing, as was also
ascertained in the investigations by K. F. Starodubov and
A. A. Sazon6va (footnote on p 174) . The fading of the
oscillations In hardened steel drawn'at a low temperature is
mainly influenced by the austenits, component whereas at
drawing temperatures above 3000 the ferrite structure becomes
decisive. There are 4 figureep I table, an& 2-3oviet
references*
ASSOCIATION# Tal'skiy mokhaniobaskiy Institut (Tula institute of
mechanics)
Card. 2/2

18(3) ^f)V
/12~?-50-7-14/25
AUTHOR: Frishtall M.N., Candidate of TechnicP1 "ciences

TITIE; - --------------
~Teutralizing Chromium -in ','allepble Tron
IIERIODICAL: Titeynoye Proizvodstvo, 1017c, ?Tr 7 74-7c (TTC?7T)N
ABSTRACT: ~s is rell lrnovm chromium even in small nmoiintq
blocks the process of grnphite formation. I~cience is
occupied with Vie acceleration of this process and
the author himself has already written several ar-
ticles on the influence of cobalt, bismuth, etc. on
the formation of new groupings of etors. V-erefore,
the author has done experiments to neutralize the
chromium during the production of cast iron in order
to allow the formation of ErRp,hite. I.- a basic mate-
rial cpst iron with a contents of chromilin of 0,251"t
has been used. An exactly measured amount of antimony
Ob) has been admixed to have an exact kno,.~:leige of
- IT
the proportion of the atoms (!T
). Tjje results
,b
cr
Card 1/2 of the research on the formation of graphite are lis-

~O
3 11/12~-59-7-14/25
Neutralizing Chromium in !Iallenble Tron
ted in one table. The formntion of frrap',lite appeprs
ap a function of the conten"s of antimony. The pro-
ces3 of grnphite formation lasts 6 to 7 times lonlyer
in case antimony has not been nVed. The foundry ex-
periments and the analysis had I~een made t'7e ag-
sistance of P.A. Tyzlov. The experiments 'have shoi,.m
that the most. favorable proportion of IT sb or is
equal to a ratio of 2 : 3. T!,ere are I"' d'La,-,rrms, 77
microphotographe and 11 ",oviet references
Card 2/2

9,5-ig 0
AUTHOR: Krishtal, M. A.
2C.-'e'--5-37144
TITLE: Estimation of the Vacancy Conoentration in Gamma-Iron
the Internal Friction Method (Otsonka kontsentratsii
vakanaiy v gamma-zheleze metodom vnutrennego treniya.)
PERIODICAL: Fizika metallov i metallovedonlye, Vol 7, Nr 3, pp
(USSR)
ABSTRACT: Slightly Abridged Translation.
Cara 1/1~
by
IVN
469-470
The peaks of Internal frietion Rt low temperatures-in
interstitial bod"entred cubic solid solutions are associated
with diffusion redistribution of the dissolved atoms under
the action of applied forces (Ref.1). Carbon atoms dissolved
in alpha-iron are In the octahedral pores of the lattice and
create distortions which change the tetragonal aymmetry. In
the absence of stress the distortion axes are evenly dia-
tributed between the three dixeotions 1001, 010: and
fOOlj. The force applied along one of' thos'e directions
leads to such a redistribution of atoms that the axes of
tetragonal distortions lie along the line of action of the
force, since stresses are partly removed, The change of

Estimation of the Vacano-y Concentration in Gamma-Iron by the Internal
Friction Method
deformation lags behind the it-angq In stress, which leads
to internal friction. The atoms of oarbon in the vacancies
do not lead to tetrahedral citst;ortiona and oan give internal
friction peaks only if their conaentration is great. if
the carbon concentration J.3 iOW, peaks are absent. Therefore
it appeared probable that a super-saturation of iron with
vacancies would lead to a lowering of internal friction peaks.
A calculation of the co ncentratlon of -the carbon which bLad
gone to the vacancies will enable ths Vaoancy concentration
in the specimen to be estimated.
The number of vscancie.,% in metala Increases with rise
in temperature. An Investigation was oarried out with wire
specimens of Armco iron, 0.5 mm diameter and 320 mm long,
which had been quenched frem 1250 and 13700C (i.e. from the
.gamma-region). Heating was sarried *ut in quartz ampoules
of-rall diameter which hadbeen evac~uated to a pressuro of
10 mm Hg. Quenching was r;aLrried cut together with the
Card 2/jr, ampoule in cold water. The motol (,ontained 0.013;~ 0,
0.02% 11n, 0.008% P, 0.023;1:4~ S aud traces of Si.

41
.0 7 ? 30
SOV/12E-7-3-37AA
Estimation of the Vacancy Concentration In Gamma-lron by the Internal
Friction Method
It was assumed that the vacancies formed on heating
are filled by0carbon atoms. Speeimena were soaked at
1250 and 1370 G for 40 minutes each. There will be
insufficient time for the vacancies forming in quenching
during the Y ---> Of transformatUn to be filled by oarbon
atoms, as it takes only about one second. It appears probable
that the vacancies formed at a high temperature will be
"marked" by carbon atoms.
The results of Internal friction measurement with a
totsion. pendulum at an oscillation frequency of 1.35 cycles
per second are shown in Fig.l. The curve for unquenohed
Armoo iron of the same composition, taken from the work of
Fao-tsuy Yunt et alia (Ref.2), is also shown. The
internal friction peaks become lower as the quenching
temperature is increased.
In the table on p 470 results of treatment of experimental
data regarding the exposure of carbon in solution and that
Cald 31j~ having gone into the vacancies, are ahown on the basis of data

Estimation of the Vaoaney Concentration in Gamma-Iron by the Internal
Friction Method
by Plmo-tnlui * Y~n et alli (Ref.2) and Dijkst-ra et alii (Ref.3).
The vacancy conoentrations obtained are comparable with
data by Lazarev et alii (Ref.4) in which it la shown that
other face-centred cubic metals, e.g. gold and platinum,
at the melting temperature have 0.1 at.% vaeanoies.
There is 1 figure, 1 table and 4 references, of which 3 are
Soviet and 1 English.
ASSOCIATION: Tullskiy mekhanicheskiT Institut "T_-_1'% Mechanical
Institute)
SUBMITTED: February 28, 1958
Card 4/4

sov/126-7-4-11/26
AUTHOR: Krishtal....
TITLE: On the Volume and Grain Boundary Diffusion
PERIODICAL: Fizika metallov i metallovedeniye, 1959, Vol 7, Nr
PP 565-571 (USSR)
ABSTRACTt After discussing the fact that the relative importance
of the part played by the volume and grain-boundary
diffusion often depends on the thermal history of the
metal or alloy under consideration and that, according
to some workers (Ref 6-8) the ratio between the
coefficients of the volume and grain-boundary diffusion is often
of the order of 10 to 1o5, the author points out that
in some published papers the values of the calculated
diffusion coefficients are regarded as referring to one
or the other type of diffusion without first evaluating
the coefficient of the grain-boundary diffusion and
without sufficient experimental evidence. Thus, a
subjective factor is introduced in deciding whether the
diffusion process is of the volume, grain-boundary or
mixed type, the more so that in most cases the diffusion
coefficients are calculated from one and the same
Card 1/6 formula (Equation 1). The object of the work reported

On the Volume and Grain Boundary Diffusion
SOV/126-7-4-11/26
in the present paper was to calculate the diffusion
parameters Q and A from experimental data using
11 quations derived for the case of volume diffusion alone,
compare the obtained results with the values of Q and A
calculated with the aid of Eq (1) and use the obtained
data for evaluating the part played of the two types of
diffusion in various processes. Experimental data on the
coefficients of self-diffusion in silver and iron, and
coefficients of diffusion in iron quoted by various
workers (Ref 3. 8-11), were used in these calculations
carried out with the aid of the Dushman-Langmuir equation
D = 62 Q.,-Q/RT (2)
Nh
where 6 - interatomic distance; N - Avogardo number;
h - Planck constant; Q - activation energy of diffusioni
R - gas constant; T - absolute temperature. Eq (2) was
selected since it is in good agreement with the
experimental data on self-diffusion in tin, gold and
copl)er (Ref 13). The pro-exponentinl term of this
Card 2/6 equation contains well-known magnitudes (6, N, h) which

SOV/126-7-4-11/26
On the Volume and Grain Boundary Diffusion
does not always apply to other formulae describing
the connection between diffusion parameters (Ref 14,15).
The value of 6 was taken to be equal to the shorter
interatomic distance (2.883 A for silver, 2-521 for
iron). Table 1 gives the experimental data on the
self-diffusion in silver (first 3 lines) and iron (the
next 3 lines) and on diffusion of chromium in iron (last
2 lines), represented in the form of parameters
Q (kcal/g-atom) and A (cm2/sec) of Eq (1). (Column 4
gives the reference, column 5 the type of diffusion
according to the original source: volume, mixed, grain
boundary, volume, volume, grain boundary, volume, volume,
mixed). The calculations of the value of activation
energy from Eq (2) were carried out by the section method
(Ref 16). Fig In and b show the examples of the results
on these calculations for volume self-diffusion in
silver and mixed self-diffusion in silver, respectively.
The values of the coefficients of diffusion and self-
diffusion and the values of Q and A calculated from
Eq (2), are given in Tables 2, 3, 4 and 5. The values of
Card 3/6 the diffusion coefficients D (cm2/sec) and parameters Q

On the Volume and Grain Boundary Diffusion
SOV/126-7-4-ii/26
and A calculated from Eq (2) for self-diffusion in
silver are given in Table 2, the three sets of data
referring to volume, grain boundary and mixed diffusion.
The same data for self-diffusion in iron are given in
Table 3 for the cases of volume and grain boundary
diffusion. Table 4 given the values of D, A and Q for
self-diffusion in silver for the case of volume diffusion
only but calculated from data quoted in Ref 9 and Ref 10.
The same data for volume and mixed diffusion of chromium
in iron are given in Table 5, Fig 2 shows the
temperature dependence of the values of Q calculated from
Eq (2) for: 1 - volume 2 - mixed; 3 - grain boundary
diffusion in silver; 4 5.7 - volume aelf-diffusion in
iron according to data tublished in Ref 8, 9 and 111
6 - grain boundary diffus.4,on in iron; 8,9 - volume and
mixed diffusion of chromium in iron. The values of Q at
3000C obtained by extrapolation of curves in Fig 2 are
given in Table 6 (column 3) together with values of Q
calculated from Eq (1) (column 2); column 1 of this
table gives the character of diffusion (self-diffusion
Card 4/6 in silver, self-diffusion in iron and diffusion of

On the Volume and Grain Boundary Diffusion SOV/126-7-4-11/26
chromium in iron)l column 4 gives the source of the
experimental data; column 6 gives the type of
diffusion: volume, mixed, grain boundary, volume,
volume, grain boundary, volume, volume, mixed. Several
conclusions can be drawn from the results obtained by
the present author; (1) When Equations (1) and (2) are
used for calculating the parameter A, comparable values
are obtained in the case of volume Belf-diffusion only.
(2) In the case of volume diffusion, the values of
activation energy calculated from Eq (2) decrease with
rising temperature. (3) There is a linear relationship
between the temperature and the values of activation
energy calculated from Eq (2). (4) Extrapolation of
activation energy curves determined ifith the aid of
Eq (2) gives the values of Q at 300*K comparable with
those obtained from Eq (1) in the case of volume
diffusion and self-diffusion only. Extrapolation of
these curves below 300*K shown that in the case of
grain-boundary and mixed diffusion in iron and grain-
boundary self-diffusion in silver. there are temperatures
Card 5/6 at which both values of Q coincide. The results of

SOV/126-7-4-11/26
.On the Volume and Grain Boundary Diffusion
calculations of these valuen are given ill 'ruble 7
ulldor tile following 110adingst number of tile curve ill
Fig 2; equation of the curve; character of diffusion
(self-diffusion in silver, self-diffusion in ironS
diffusion of chromium in iron); the temperature ( K)
at which 02 = Ql; type of diffusion (grain-boundary,
grain-boundary, mixed). (5) Calculated values of A and
corresponding most closely to those characteristic of
the volume diffusion were obtained from experimental
data due to Gruzin (Ref 9) and Birchanall and Diehl
(Ref 11). There are 2 figures, 7 tables and
16 references, 11 of which are Soviet, 4 English and
1 German.
ASSOCIATION:Tullskiy mekhanicheskiy institut (Tula Mechanical
Institute)
SUBMIT-TED: November 20, 1957
Card 6/6

SOV/126-8-2-20/26
AUTHORS: Krishtal, M.A. and Golovin, S.A.
TITLE: Nature of Intornal Friction in Hardened and Tempered
Steel
PERIODICAL: Fizika metallov i metallovedeniyo, 1959, Vol 8, Nr 2,
pp 294 - 301 (USSR)
ABSTRACT: Many hardoned and tempered steel parts work under loads
of varLable sign at high temperatures and the nature of
relaxation effects is thus impartial. A pronounced
internal-friction peak has been observed (I.N. Chernikov
Refs019 2) for hardened and tempered carbon stools at
200 C, the peak height depending on the carbon content and
tempering temperature. The authors describe their work
with type V-1 high-carbon steel, widely used for springs.
Two compositions (Table 1) were used: 0,71, 0,92% C;
0.47, 0.24% Mn; 0.34-0.26170' Si, respectively, with
0,02910 S, 0903% P, traces of Cr, under 0.11,19' Cu and no
Ni nor Ti. Tent pieces were 0.8 mm in diameter, 320 mm long.
Vacuum annealing at 1 000 0 C for two hours 0was carried out
Cardl/4 before hardening; hardening was from 800 C. Tempering

SOV/12~4-2-20/26
Nature of Internal Friction in Hardened and empered Steel
was effected for one hour at temperatures of 100, 200,
250, 350, 450, 500 and 700 0C. Internal friction was
measured on a type RKF-MIS-1 vacuum torsional installation
at frequencies of 1-33 and 2.08 c.p.s. Internal friction
as functions of temperature for various tempering
temperatures is given in Figures I and 2 for the 0.71
and RZ 92% C specimens. The peaks lie between 220 -
260 Acreasing inxalue with rising tempering tempera-
ture and with falling carbon content (as shown by the
data in Table 2, derived from the authors' and published
(Ref 1) data and in Figure 3). The temperature of the
peak rises linearly with increased carbon content
(Figure 4). In Figure 5, the internal-friction peak
values are shown to be related linearly both to total
carbon percentage and to percentage of residual austenite
(obtained from the work of A.P. Gulyayev - Ref 4). The
authors have calculated values of the diffusion coefficient
and activation energy corresponding to the positions of
internal-friction peaks. For activation-energy determi-
Card2/4 'nations additional internal-friction measurements were

sov/.i26-8-2-20,/26
Nature of Internal Friction in Hardened and Tempered Steel
carried out at 2.08 coposo Figures 6 and '7 show internal
friction plotted against temperature for the 0.71 and
0.927/0 C steels, respectively, hardened from 800 C.
Curves I and 2 in Figure 6 (.orrespond to frequencies of
1-33 and 1.81 c.pos. and to frequencies of 1-33 and
2.08 in Figure 7, a second pair of ~.,urvte in the latter
corresponding to steel tempered at 250 *"-. Tables 5. 4,
and 6 show diffusion-coefficient values for carbon in
the 0.92- and 0.73N-C carbou steels, respectively;
Tables 5 and 6, based on published (Ref 1) data, give
the values for steels with 0.58 and 0.46% C, respectively.
The results agree with published (Ref 8) indications
that the rate of diffusion of carbon is lciss in austenite
subjected to hardening than in austenite not so treated.
Diffusion-coefficient values measured by the internal-
friction method for hardened steel tempered a'. low tempera-
tures agree with those found metallographically in
austehite obtained from the hardened state. As a further
Card3/4

SOV/126-8-2-2o/26
Nature of Internal Friction in Hardened and Tempered Steel
check the internal friction o6 0.92% C steel subjected
to double hardening from 800 C was determined, showing
a displacement of the internal-fription peak towards
higher temporatures (Figure 8 - Curve 2 compared with Curve
1).
Professor B.N. Finkel'shteyn, Yu#V. Piguzov, L.F. Usova
and I.N. Chernikova helped in internal-friction
measurements. There are 8 figures, 7 tables and
10 references, of which 8 are Soviet, 1 English and
1 international.
ASSOCIATION: Tul'skiy mekhanicheskiy institut (Tula Mechanical
Institute)
SUBMITTED: February 28, 1958
Card 4/4

SOV/126-8-2-21/26
AUTHORS: Krishtal, M.A. and Golovin, S.A.
TITLZ~ Contribution on the Nature of Relativo Damping of
Oscillation in Hardened and Low-tempered Carbon Steel
PERIODICAL: Fizika metallov i motallovedeniye, 1959, Vol 8, Nr 2,
PP 302 -- 308 JUSSR)
ABSTRACT: The authors' previous (Refs 1, 2) measurements of
m1cro-plastic Internal friction in heat-treated type
50A and U`7A steels and of internal-friction relaxation
in U7A and-UgA steels showed the great effect of
residual austenite in hardened emd low-tempered specimens
on the damping capacity of the rteel. Their Iresent
investigation, aimed at further examination or this
postulate, was carried out with 50A and U7A &teels
(widely used for machine parts tubjected to vibration
in service) of the following reopective percenta a
composition; 0*49, 0-70 C: 0.34, 0.23 Mn; 0. 59, 0.18 51;
0.024, 0.021 S; 0.019, 0.026 P; 0.19, traces Cr.
An apparatus (Figure 1) was provided with tensometric
Cardl/3 recording of vibration patteins and with a furnace

SOV/126-8-2-21/26
Contribution on the Nature of Relative Damping of Oscillation in
Hardened and Low-tempered Carbon Steel
enablino the 7-mm,0diameter test pieces to operate at up
to 36o C with 10 intervalS in a protective atmospbero.
Before hardening (from 800 C for U7A and from 860 uC
for 50A steel) specimens were annealed for one hour;
hardening was followed by tempering for one hour at
different temperatures. Tte effect of repeated-stressing
treatment on relative damping for the two steels is shown
in Figures 2 and 3. In the higher-carbon steel repeated-
stress treatment gave reduced relative damping at higher
stresses. The treatment did not increase hardness.
Holding In liquid nitrogen was found to reduc8 relative
damping for tempering temperatures up to 200 C (Figures
4 and 5 show this property as a "function of stress for
various heat-treatment histories for the two steels).
Repeated hardening also reduced relative damping (Curve 2
compared with Curve I in Figure 6). A maximum of relative
damping was found for U7A steel at about 290 OC in tests
with continuous heating (Figure 7). The authors used their
Card2/3 own and published (Ref 1) data to calculate the carbon

SOV/126-8-2-21/26
Contribution on the Nature of Relative Damping of Oscillation in
Hardened and Low-tempered Carbon Steel
diffusion coefficientt diffusional relaxation in austenits
evidently playa some part. Their results indicate that
residual austenite has a considerable influence on the
damping properties of the hardened and low-tempered steels
investigated (Figure 8 shows relative damping at various
atrossas plotted against time of tampering at 200 0C for
U7A steel). There are 8 figures, I table and 9 references,
7 of which are Soviet and 2 English.
ASSOCIATION: Tullskiy makhanichookiy institut (Tula Mechanical
Institute)
SUBI,aTTED: August 22, 1958
Card 3/3

KRISHTAL, M.A., kaTA. tekhn. nauk, dote.; FVMIlr=l I.P., kand, telchn. nauk, dot$@;
MEW, V.F., kand. takhn. nauk, 4ote,; TSETTLIN, A*Y&,, insh,
Characteristics of the surface structure of decarburized malleable
Iron castings and their machinability. Trudy TMI no.11:66-77 159-
(nft 12:12)
(Cast trarr-Heat tr6atment) (Metal outting)
i

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;.Os . ,, lgr-o, 51 pl) ("os.,;o.; Stec

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31

AUTHORSt Krishtal and Titenskiy, E. G.
S/12 60/0UU/009/001/003
A161 YA133
TITLE: Modified malleable cast iron with hi&h chrome content
PERIODICAL: Liteynoye pitizvodotvol no. 9, 1960, 33-35
TEXT: As it is known, chrome is the strongest inhibitor of the gra-
phitization process in malleable cast iron, and its usually permissible maxi-
mum content is O.Or/.. more chrome is getting into cast iron with high-alloy
steel scrap, and ways must be foun4 to neutralize its effect. This is pos-
sible by the addition of silicon and aluminum [Sobolev, B. F. - Ref. 2: go-
difitsirovaniye i isakustvennoye stareniye kovkogo chuguna (Modification and
artificial aging of malleable cast iron), Mashgiz, 1956], or by'the addition.
of manganese. But the greatestattention is paid now to the addition of an-
timony (Krishtal, M. A. - Ref- 3t DAN SSSR, v. 99, no- 4, 1954; Livshits,
B. G. - Ref. 4t DAN SSSR, v. 93, No. 6, 1953; Krishtal, U. A. - Ref. 5t Li-
teynoye proizvodatvo, no. 8, 1959). This article presents data obtained in
an investigation with additions of antimony and-boron, and combinations of
boron with bismuth, and boron with antimony. Boron was added in the form of
Card 1/5

S/128/60/000/009/001/003
Modified malleable cast iron with... A161/A133
ferrosiliconboral and ferrobcron in amounts of 0.003 - O.Q10% of the weight
of iron. Antimony and bismuth were used in metallic form. The Gorlkovskiy
avtozavod (GorIkiy Automobile Plant) has started to utilize cast iron modi-
fied with boron and bismuth, but the mechanism of the effect of these addi-
tives on the graphitization is not yet clear and further experiments are nec-
essary. Four alloy groups were studied (the compositions are given in the
table). The results prove that the graphitization time is shortest at a
weight per cent ratio of antimony and chrome of 3t2, which corresponds to the
formation of atomic segregation's of the Sb2Cr3 type. Annealing for 36 hours
as illustrated in diagram (Fig, 1) resulted in malleable cast iron with gra-
nular pearlite metal Fig. 2,a ; no primary carbides formed with a chrome
content of up to 0.2%~ The mechanical properties of metal modified by Sb
alone are given in curves (Fig. 3): hardness and strength increasing with a
rising Cr-content, the plastioity decreases; at 0.10,'o Or the elongation is
5%, at 0 2% Cr it is-2.6%; the ultimat4 strength and hardness incresse'to
50 kg/mm, and HB235; the machinability remains good de spite high hardness.
Contrary to 3b only, additions of B and Bi resulted in 5 - 8% eutectic car-
bides even at a low Cr-content (0.06%) and meohanical properties as in Figure
4. The residual carbides did not affect the machinability because of the en-
Card 2/5

-!1 on/ 0 /0 C A 0fc- C, I /C0' 3
malleable ca:;. ixuii A1131/A133
voloping graphite, and at UP to 0.10~,~ th4, cloneation did not drop below
the strength reached 40 - 42 ko/mm2, and hardneso HB157- An increase in the
chrome content over 0.101,11, resulted in some decrease of the impact strength.
'This modification method yielded forritic high-chrome iron with low hardness
and hiCh elongation. Iron modified with boron only had a sufficiently hi;;h
Craphitization capacity. Bismuth is a very inconvenient additive - it.burns
with copious fumes separation. Antimony is a chemical equivalent of bismuth,
and it has the samechilling effect and dissolves well in iron, whil3t liquid
iron and bismuth do not mix at all. The plasticity of iron modified with 3
and Sb remains high with up to 0.2j'a' Cr,')and tho elonGation is about 7rfi; the
str~!ngth and hardness are increasing with a risinG Cr-content. The higher
hardness is due to the presence of a small quantity of pearlite (Sb prevents
graphitization in the second stage). The machinability is not affected by
residual pearlite. In general, the machinability of iron modified with borcn
and antimony, or with boron ard bismuth is practically eame. Antimony (like
bismuth) gives an isotropic iron structure. Modification with antimony is
not accompanied with any fumes separation. 3oron alone may be used for thin-
walled castings (5 - 15 mm), for no graphite separation takes place durinu
crystallization. The optimum boron addition for 15 mm wall castings is
Card 3/5

S11201601000100910011003
Modified malleable cast iron with... A161/A133
0.003 - 0.005$. The impact atrength of iron modified with boron only drops
abruptly with An Inorwing ihromo content# which appoore to be duo to ani.
eatropy but it does hot affeat the dhor madhatiaid PrOpettidd. The tiadhin-
ability of boron-modified iron did not differ from the usual in malleable
iron or in iron modified with other additives. There are 6 figures and 8
Soviet-bloc references*
Ic
700
WO
sea
0.

17
Figure It
The annealing grapht temperature'in
OC and time in houre (to 37 hours).
Card 4/5

M,odified malleable caEit iron
"161IA133
q
yry U
L. a C 51 Ain S P Cr At Sb

I MO
ov.. 2,72-2,62 1,14-1.27 0.&)-0,55 0.126-0.1= 0,074 0,70-0.20 0,015-0,C"0 0,12-0,3D
11 1t-
MO 11
w
1
=
8
rc.vTo- 2,W-2,15 1.16-1.?2 0,53-0,58 0,22-0,143 0^2 0.01-0,16 0.013-0,c-0 - 0.003-0005 0.01
III MOA1OOp"W.POB2"-
out 6apow . . . 2,61-1.72 1.12-1.23 0,41-0,53 0.0-0,143 0." O.CS-0,14 0,015-0,0M - 0.0C3-0.01 -
IV M
nut 69p9w K
I.P-2.79
1.10-1.30
0.49-0.81
0.120-0,135
0.072
0,01-0,20
0,015-0..20
O.WS-O.Ml
O.W3-0.fts
-
Table: I Iron modified with Sb; II with B and Bi; III - with B only;
IV - with B and Sb.
~1~ chemical composition.in 1744;
2 addition of modifier in-%.
Card 5/5

s/i26/6o/oo9/O2/033/O33
AUTHOR: Krishtal, M.A* Elll/E335
I------------
TITLE: Special Features of the Influence of S-ilicon-on the
\:,Diffusion of Carbon in Austen�te,'i
PERIODICAL: Fizika metallov i metallovedeniye, 1960, Vol 9, Nr
pp 317 - 319 (USSR)
ABSTRACT: The author notes that the results of his metallographic
investigation of the influence of silicon on the kinetics
of carbon diffusion in iron-carbon alloys'](Ref 3) differ
from those of others (Refs 11 2); this has led to
confusion (Ref 4). He has now added precision to his
previous results and extended his measurements to higher
temperatures. Using his previous method (Ref 3) he has
studied diffusion durin 6 annealing at 860, 880, 920, 950,
1 000, 1 050 and 1 100 Ce The data in Table 1 show
that at 1 100 dog an increase in the silicon content reduces
the diffusion coefficients at 1 000 and 1 050 OC it has
little effect and at 950 C and below it increases diffu,!~~$
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S/126/6o/oog/02/033/033
,P j5~jl, E 3 3 5
Special Features of the Influence o icon on the Diffusion of
Carbon in Austenite
There are 2 tables and 8 references, 6 of which are
Soviet and 2 English.
ASSOCIATION: Tul'skiy mekhanicheskiy institut (Tula Meohanical
Institute).
SUBMITTED: December 3, 1959 40,
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)STO S/i26/6o/oo9/O5/oo6/o25
AUTHOR: Krishial, M.A. Elll/E335
TITLE: Diffusion of Several Elements from One Source in Iron and
its Alloys
PERIODICAL: Fizika metallov I metallovedenlye, 196o, Vol 9, Nr 5,
pp 680 - 688 (USSR)
ABSTRACT: The object of this work was to develop the method for
investigating the diffusion of several elements from a
single source and make a qualitative evaluation of the
influence of some alloying elements. The localized spectrum-
analysis method of I.L. Mirkin and E.P. Rikman ( Ref 1) was
used, giving a diameter for the working part of the sparked
area as low as 0.05 mm, or the spark operates between the
section and an edge up to 0.1 mm thick. The source was
electrolytic iron alloyed with 0.0120% C, 0.0231,10' P, 0.01410' S
and 2.5110 each of Cr, Mn, Si, Mo and Ti. Diffusion was
studied into iron and also into binary alloys with 5 at
Of Cr, Si, Co and V. Figure I shows distribution of
chromium"Ailicon andvKanadium with depth in diffusion
layers of specimens made up of iron-silicon, iron-chromitun
Cardl/3 and iron-vanadium alloys and electrolytic iron. The
LK

0527
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Diffusion of Several Elements from Onllellg&M in Iron and its Alloys
ordinates in this and all other figures in the paper show
tho difference between the degrees of darkening of the
analytical pair of spectrum linen. Figure 2 shows distri-
butions of chromium, silicon and vanadium in a single
ferrito grain for diffusion from the multi-component
source. Figure 3 shows distributions of titanium,
manganese, silicon, chromium and molybdenum diffusing from
the complex alloy (lefthand figures in abscissae) into ironi
the corresponding curves for diffusion into the binary
iron-chromium alloy are shown in Figure 4, into the binary
iron-silicon alloy in Figure 5, into the binary iron-
vanadium alloy in Figure 6 (which includes a curve for
vanadium) and into the binary iron-cobalt alloy in Figure 7.
Figure 8 gives the titanium-distribution curves for diffusion
into all the binary alloys and iron; Figures 9, 10 and 11
give the corresponding curves for manganese, chromium and
silicon. From these figures the influence of each alloying
element on the diffusion -of each element can be estimated:
the author gives values on this influence. The work showed
Card2/3 that the rate of diffusion increases in the following order:

2 CS 2.7
S/l26/6o/oo9/05/oo6/025
Diffusion of Several Elements from 0111140M in Iron and its Alloys
titanium~ manganesk';,~ chromium, silicon and molybdenum~4
All the alloying elements of the binary alloys reduce the
diffusion rate, this effect being the more marked the
slower the diffusion rate of the diffusing element in iron.
Cobalt had the greatest effect on diffusion, which the
author attributes to its pronounced effect in reducing
isothermal austenite decomposition in the presence of other
elements. Professor I.L. Mirkin assisted in discussion of
results and E.P. Rikman and N.I. Peshkova in the
experimentaf work. re are 11 figures and 4 Soviet
references.
ASSOCIATION: Tullskly mekhanIcheskiy institut (Tula Mechanical'it/
Institute)
SUBMITTED: October 16, 1959
Card 3/3

KRISHTAL. M.A.1 RIMWP E.P,
-
Distribution of elements in a complex iron-base alloy. Piz.
met. i metalloved. 9 no.5:790-792 My 160, (MIRA 14t4)
1. Tul'skiT mekhanicheekly institut.
(Iron alloyow-Metallography)

3/126/6o/oiLO/02/015/020
ER~K
AUTHORSt Piguzov, Yu.V Krishtal, NN Golovin, S.A.
TITLE, The Nature of t;o Maximum of Internal Friction in
Steel After Thermal Treatment -116
PERIODICAL: Fizika metallov i metallovedeniye, 1960, Vol. 10,
No. 2, pp 285 - 290
TEXT: Experiments were carried out on three steels - U7A, U9A
and U12A - the compositions of which are given in Table 1.
Measurements of internal friction were taken on a mlaxator at
a frequency of 1 cps. Results for two steels are given in
Fig. 1, where the internal friction is plotted against tempera-
ture. The curves contain the usual maxima at 200 0C. The curves
with the higher peaks are for the steel with the greater amount
of carbon. The absolute values of the peaks are given in
Table 2. Working in the cold leads to a decrease in the value
of the peak corresponding to the decrease in the retained quantity
of austenite. Fig. 2 shows the internal friction - temperature
curves for U9A steel after quenching from sub-critical temperatures
(720 0C and 670 OC). A low maximum is obtained at 200 OC, much
less than that after quenching from the austenitic condition.
Thus, the 200 OC peak can be explained by two phenomena taking
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2021/9333
The Nature of the Maximum of Internal Friction in Steel After
Thermal Treatment
place simultaneously: diffusion of carbon atoms in the retained
austenite6'and migration of carbon atoms to the dialocdtion regions
forming on account of the martensitic transformation and thermal
stresses. Further experiments were carried out on armco iron
containing 0.019% carbon after 250,; and 75% deforzation. Fig- 3
shows the curvaCs obtained. Deformation of 25% leads tootwo peaks
at 40 and 200 0 75% deformation gives one Teak at 20 'C. The
disappearance of the first peak can be explained by migration of
carbon atoms in the alpha-iron to more energetic positions - in
dislocations. The peak at 200 0C is much lower than for quenched
steels because of the smaller amount of austenite.
There are 2 tables, 3 figures and 10 references: 2 German$
2 English and 6 Soviet,
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S/126/60/010/02/015/020
E22j/
The Nature of the Maximum of n WN Friction in Steel After
Thermal Treatment
ASSOCIATIONS: Tullskiy mekhanicheakiy inatitut
(Tulsk Mechanical Institute
Moskovskiy institut stali im. I.V. Stalina
Moscow Institute of Steel im. I.V. Stalin
SUBMITTED: Penruary 18, 1960
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Elll/E452
AUTHOR. Krishtal, M.A.
TITLE: Concentration of Vacancies in Iron-Chromium Alloys
PERIODICAL:Fizika metallov i metallovedeniye, 1960, Vol.10, No.5,
PP-720-726
TEXT. The author criticizes evaluation (Ref.1,2) of vacancy
concentration from measurement of electrical resistivity of quenched
specimens: the temperature vs vacancy concentration relation could
be distorted by polymorphic changes. He recommends measurement of
resistivity during heating to high temperatures and describes his
work on this. he wire specimen was held (Fig.1) at a pressure of
the order of 10-3 mm Hg in a quartz U-tube in a furnace at up to
1400"Ci the ends of the tube were outside the furnace and the
specimen ends passed out through rubber bungs and were connected to
a type MOA -49 (MOD-49) bridge. The range of compositions W
covered was 0.013 to 0.040 C, traces and 0.02 Mn, traces - 0.011 Si,
o.oo8 to 0.030 P. 0.010 to 0.023 S, 0 to 5.72 Cr. Resistivity
was found to increase linearly with chromium content (Fig.2).
Fig.3 shows, for the 5-72% Cr alloy, resistance as a function of
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85965
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Elll/E452
Concentration of Vacancies in Iron-Chromium Alloys
temperature: above 11400C the experimental points deviate from the
atraight line. Table 2 gives resistance changes and temperatures
for the various alloys: linear relations were obtained between the
logarithm of resistance change and reciprocal of absolute
temperaturo (Fig.4), the corresponding activation energies for
vacancy formation increasing from 93800 cal/g atom for Armco-iron
to 31200 for the 5.72% Cr alloy. Vacancy concentrations
calculated from these results for Armco iron and each of the alloys
are given in Table 3. They were checked by the internal friction
method already described by the author (Ref.6): the internal
friction peak at 40% in determined for specimens with and without
vacancies, the concentration being found from the difference.
Vacancies were created by heating in vacuum to 1050 - 13700C and
quenching. Results for the 0.85% Cr alloy are shown in Fig-5 as
plots of internal friction against temperature for various
quenching temperatures. Table 4 like Table 3, shows that vacancy
concentration rises regularly with higher heating temperature and
lower chromium content. Table 4 also gives carbon concentration in
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S/126/6ow/005/013/030
E111/E452
Concentration.of Vacancieb in Iron-Chromium A11oyB
the solution and in the vacancies. Extrapolation suggests that
at the melting point, vacancy concentration is about 0.1 at.%.
There are 5 figures, 4 tables and 7 references: 5 Soviet and
2 Non.-Soviet.
ASSOCIATION: Tullskiy mekhanicheskiy institut
(Tula Mechanical Institute)
SUBMITTED;; March 29, 1960
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8/123/61/000/011/020/034
A0041AI01
AUTHORSt Krlshtal,_M.-A.1 PomWkh, I. P.1 Lyzlov, B. A.
'TITU: Properties, structure and maohinability of malleable cast iron with
chromium and antimony for fittings
PERIODICALi Referativnyy zhurnal, Mashinostrayoniye, no. 11, 1961, 3, abstriot
11018 (qSb. tr. Tul'sk. maknan. In-ta", 1960, no. 15, 20-26)
'TECTs An increase In the chromium content of the metal, when alloyed steel
gets into-the charge, causes a considerable prolongation of the annealing cycle
and also tool breakage during the working of-fittings an a result of insufficient
annealing in the first stage. Investigaticna showed that a Cr-content of 0.15%
in neutralized by the addi-tien of 0.23% Sb to the cast Iron. S&at iron contain-
Ing ?.56% C, 1.5% Si, 0.15% Cr, 0.23% Sb6 Lfter heating to 960 C for 3 hours
holding of 15 hours, cooling down to 720 C for 2 hours and holding at this
temperature for 10 hours, had the structure of pearlits malleable cast Iron of
the Kq-54-5 (KCh-54-5) grade. Tests of the machinability showed that in the
time interval between the sharpening of the taps 5-6 times more fittings from
malleable cast iron alloyed with chromium and antimony (HB 170-200) could be
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S/123/61/000/011/020/034
Properties, structure and maohineability ... A004/A101
machined than those of ordinary non-alloyed cast Iron. There are 3 figures.
L. Tumanova
[Abstracter's notat Complete translAtion]
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S/137/62/oco/oWoWi63
Af6O/AIOI
A1111TORSt Mirkin, 14'L-1 Irishtal, M. A.
TITLEf The thermal mobility of atoms In alloys
PFR[ODICAL: Reforativnyy zhurnal, Metallurgiya, no. 6, 1962, 7, abstract 6143
(In oollectiont "Iasled. novykh zharoproohn. splavov dlya energe-
tiki". Moscow, Mashgiz, 1961, 5 - 33)
TEXTi Review. Discussed are the meohanisms of diffusion: the diffusion of
the pair exchange, along the vacancies, along the interstices, and the annular
diffusion., The results of work carried out on the determination of concentration
of vacancies by the methods of measuring tbe electric resistance of alloys and
of the internal friction are presentedi The effect of the volumetric factor on
the diffusion of elements dissolved by the principle of interstitial atoms-is
considered.. As regards the diffusion of H, N, C;-ard-B, a linear dependence of
the energy of activation on the atomic diameter of the element was detected in
ol-Fe, In the case of diffusion along the Interstices, the valence of dissolved
,~~Iewents has a secondary importance. The diffusion of elements dissolved in
-;,ar,d 1/2

S/137/62/00()/006/09Z/163
The thermal mobility of atomn in alloys A160/AI01
Fe-94,J NI-by the-principle of substitution is discussed in detail. The results
of work on the investigation of simultaneous diffusion of several elements from
on,:~ source are given. The effect of the structure on diffusion is investigated.
tilrfaoe dAffuzion and the dependence of diffusion on crystallographic orienta-
tI-_,n are disrussed. There are 49 references.
I. Leftonov
J'Arstracterlz note; Complete translation]
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30454
11 OD 114 64 S/126/61/012/003/009/021
Jr.193/Z135
AUTHORSt -Krishtal, M.As-, and Mokrov, A.P.
TITLE% work hardening of surface layers formed by diffusion
of -nolybdenum into iron and its alloys
PERIODICAL: Fizika metallov i metallovedeniye, vol.12, no.3, 1961,
389-394
TEXT: One of the shortcomings of the diffusion method of
surface-hardening of metal components is that they produce
diffusion layers whose hardness and strength decrease with the
distance from the surface. Means of attaining uniform-mechanical
properties across such diffusion layers are required, and a
possible method for achieving uniformity in the mechanical
properties in described In the present paper. The method proposed
is based on the fact that (a) the variation of hardness is
ass6ciated with the gradient of the alloying element concentration
across the thickness of the diffusion layer; and (b) the rate of
work-hardening of ferrite decreaseis with increasing content of
alloying additions. Consequently, a diffusion layer subjected to
plastic deformation should work-harden most in its softest part
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V

3045h
Work hardening of surface layers S/126/61/012/003/009/021
E193/EI35
and least in the hardest region with the maximum concentration of
the alloying additions. To verify this proposition a series of
diffusion experiments were carried out. Diffusion couples were
formed by a mo2ybdenum foil (0-04-0-05 mm thick) sandwiched
between strips of iron or one of the five types of iron-base
alloys, containing up to 5 at.% Co, Si, Cr, W, and V. Good
contact at the diffusion interface was ensured by spot-welding the
components in hydrogen, after which they were subjected to a
vacuum diffusion treatment for 10 hours at 1250 OC. Each diffusion
couple was sectioned, and microhardness, H,,l measurements were
taken across the thickness of the diffusion layer at regular
intervals. Each type of the specimen was then compressed to 10,
20, 30 and 40% reduction in thicknoss, after which the micro-
hardness measurements were again carried out, the degree of
localised deformation c, S. in the diffusion layer being deter-
mined from the decrease in the distance between the original
microhardness tester indentations. From these data the so-called
specific microhardness &HII/c (where 6HV& is the increase in
H~j due to deformation c) was determined which gave the measure
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Work hardening of surface layers S/126/61/012/003/009/021
E193/EI35
of work-hardenability of a particular region of the diffusion layer.
The results are reproduced graphically, those obtained for the
5 at.% Co-Fe alloy being shown in Fig-3 where H,, (kg/MM2, left-
hand scale), LHp/c, and c (%, extreme right-hand scale) are
plotted against the distance (mm) from the surface of the
diffusion layer formed by diffusion of molybdenum. Circles and
squares denote Hp before and after 40% total deformation,
respectively; the variation of localised deformation c in a
specimen deformed to 10% reduction in thickness is denoted by white
triangles, black triangles relating to specific microhardness
(AHIA/c) of specimens deformed to 40% reduction in thickness.
Analysis of these and other results showed that hardness of the
diffusion layers studied varied across their thickness in accordance
with the variation of the molybdenuts content. The effect of plastic
deformation (compression) on the variation of H$Ll C, and t4 HO/C
across the thickness of a diffusion layer was also dependent on the
molybdenum content, the regions of low Mo content being
preferentially work hardened. This proved the possibility of using
plastic deformation to attain grantor uniformity of mechanical
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Work hardening of surface layers S/126/61/012/003/009/021
E193/E135
properties across surface diffusion layers. The beneficial effect
of plastic deformation wa3 most pronounced in the diffusion layers
formed by molybdenum in the Fe-Si, and least noticeable in the
Fe-V alloys.
There are 7 figures and 12 references: 4 Soviet-bloc, 4 Russian
translations of foreign language articles, and 4 non-Soviet-bloc*
The English language references read an followei
Ref.2: C. Austin. Trans. ASM, 1943, Vol-31, 321.
Ref.4: C. Austin, L. Luite. R. Lindsay. Trans. ASM, 1945, Vol.35,
446.
Ref-5: C. Lacey, M. Gensamer. Trans. ASM, 1944, Vol.32, 88.
ASSOCIATION: Tullskiy mekhanicheskiy institut
(Tula Mechanical Institute)
SUBMITTED: December 19, 1960
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32660
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19 11511 EO4O/E435
AUTHORS: Krishtal, M.A., Baranova, V.I.
TITLE: Internal friction and electrical resistivity of ferro-
.chromium alloys
PERIODICAL: Fizika metallov i metallovedeniye, v.12, no.5, 1961,
768-771
TEXT: Due to the ease of formation of chromium carbides, the
mobility of the carbon atoms in solid solutions of ferro-chromium
alloys can be appreciably affected and with it the mechanical
properties of the metal. The problem was examined by determining
the kinetics of carbides dissolution in chromium-containing solid
solutions during their heating prior to quenching. For this
purpose, measurements were made of the internal friction and
electrical resistivity of wire-shaped specimens 0.7 mm in diameter
and 160 mm long. The specimens were completely annealed by
holding for 2 to 3 hours at 10500C and quenched in water from
720 to 12000C. Before quenching, the specimens were heated in
vacuo for 10 to 40 minutes, depending on the Cr content.
Internal fri~ction -was measured by the torsional pendulum method in
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32W)
S/126/61/012/005/022/028
Internal frittion and electrical ... Z040/E435
vacuum relaxator apparatus. Annealed specimens containing
chromium carbides were found to have no internal friction maximum
on the temperature curve. However, specimens quenched from
800*C gave internal friction maxima corresponding to 30 to 40 and
170"C. The actual value of the internal friction peak risen with
increasing temperature of quenching, reaches its maximum for the
quenching temperature of 1050'2C andthen drops. The height of
both internal friction maxima was found-to be dependent on the
chromium content in the alloy. The specific resistivity of the
specimens diminishes with increasing quenching temperatures (up to
1100*0 and passes through a minimum at 1050'C but it increases if
the specimens are quenched from temperatures exceeding about 11100"C,
It is conpluded that an increase of the quenching temperature
leads to progressively higher carbon contents of the solid
solution because of the rising solubility of chromium carbides.
The concentration of carbon at points of its introduction into the
solid solution rises up to a temperature of 1050*"C,, while further
heating above this temperature leadis to the formation of vacancies
which tend to be occupied by carbon atoms shifting from the points
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32660
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Internal friction and electrical EO4O/E435
of their original introduction. The lower temperature internal
friction maximum (30 to 4000 is believed to be connected with
carbon migration in the stress field around the iron atoms. The
high temperature internal friction maximum (170*0 is thought to be
connected with the migration of carbon atoms in the solid solution
around the chromium atoms and, perhaps, with their migration to
positions surrounded by iron atoms. There are 4 figures and
5 Soviet-bloc references,
ASSOCIATION: Tullskiy mekhanichesiciy institut
(Tula Mechanics Institute)
SUBMITTED: March 20, 1961 (initially)
May 8, 1961 (after rovision)
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