SCIENTIFIC ABSTRACT SELISHCHEV, K/P. - SELISSKIV, YA.P.

• Document Type: CREST
• Collection: Scientific Abstracts
• Document Number (FOIA) /ESDN (CREST): CIA-RDP86-00513R001547720011-3
• Release Decision: RIF
• Original Classification: S
• Document Page Count: 100
• Document Creation Date: November 2, 2016
• Document Release Date: August 23, 2000
• Sequence Number: 11
• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTRACT

S/1?3/62/000/009/005/009
A054/A127
AUTHORS: Kolmogorov, V.L., Candidate of Technical Sciences, Selishchev,
K.P., Engineer
TITU"': Cold drawing of tube6 under Improved lubricating conditions
r
PEKODICAL: Sral'.. no. 9. 1962, 83.0 - 831
TEXT: Tests were carried out to improve the lubrication in drawing tubes
without using mandrels. For this purpose a simple device consisting of a sleeve
and a finely dispersed clean high-viscosity sodium soap powder were used. Tubes
of "20" and 1. X1811()T O.Kh18149T) grade steel were drawn with a wall-thickness-to-
-diameter ratio varying between 0.05 and 0.13, at drawing rates of 0.17 - 0.58
/zec. The soap powder applied forms a dense, glasiy, adhesive coating, O.Ou-,
0.051. mm thick, on the tube surface, which is sufficient to prevent any diroct
contact between the drawing die and the tube surface. When this new lubrication
method is applied, the service'life of the drawing tool will beraised considerab-
ly; moreover, stainless steel tubes can be drawn by dies of 12X5MA (12Kh5MA.)
steel instead of "pobedit" (sintered carbon); the drawing power required will be
reduced by 27 - 29%, and stainless steel tubes of a higher surface quality can be
Card 1.12

# I S/133/62/000/009/005/aG9
Cold drawing of .... A054/A127
produced. An essential condition of using sodium soap powder as lubricant is
that the tube surface must be dried carefully prior to drawing. There is I
figure.
ASSOCIATION: Ural'skiy nauchno-issledovatefskiy institut chernykh metallov
(Ural Scientific Research Institute of Ferrous Metals)
Card 2/2

KOLMOGOROV, V.L.; OUOV, S.I.; ~ZLISIIGHFV, K.P.; LFYARENKO, Ya.M. [deceasad);
POKROVSKAYA, G.N.; TIYiftor, -DJC~ BOGOMOLOV, I.F.
Drawing wire of nonferrous metals and allojs in condftions of fluid
friction. TSvet. met. 36 no.12:65-67 1 163. (MIRA 17-2)

AUTHOR - Selishchev, V.I. 3-7-10/29
On Some possibilities of Improving Technical Training in
TITLE!
Correspondence and Evening Courses (0 nekotorykh vozmozhnost-
yakh uluchsheniya zaoctmogo i vechernego tekhnicheskogo
obrazovani-ya)
PERIOLICALt Vestnik Vysshey Shkoly, 1.957, # 7, Pp 45-49 (USSR)
ABSTRACTt The author states that a characteristic fact in the devel-
opment of Soviet higher schools is the considerable increase
in student training without interrupting the students' indu-
strial work. As an example the author quotes the system of
correspondence schooling used by the Ministry of Public Trans-
port which includes the All-Union Correspondence Institute for
Railway Transport Engineers (VZIIT), 4 correspondence sections
in day vuzes and 26 consultation centers all serving about
20,000 students distributed among 120 railroad centers. The
permanent teaching staff, which includes 17 professors and
69 dotsents,, is concentrated primarily in the chairs of the
VZIIT in Moscow, while about 1,000 part-time teachers - paid
by the hour - are used. The author then mentions the shortage
of laboratories and qualified teachers in the correspondence
Card 1/ 1 school system. He then suggests creating general engineering

3-7-10/29
On Some Fouoibilities of improving Technical Training in Correspondence
and Evening Courses,
and general economics faculties in the existing vuzes for
the first years of correspondence training. At the end of the
third year, the assignment of the students to certain institu-
tions should be made in accordance with their special ties.
The assignment to a specialized school after the third year
should not mean a transfer to a remote institute of the special
branch, since special faculties may be reorganized in any
nearby related technical v-uz. He mentions sev--ral vuzes where
this has been done and 3everal where it could be done and
adds that it must be understood that the suggested reorganiza-
tion should be applied also to methodical management. In this
connection the vuz bases will play an important part. For
many special ties one important vuz base would be sufficient;
however, in some cases, methodical management could be assigned
to vuzes situated in different economic areas.
Finally the author mentions some of his observations relat-
ing to evening courses in technical vuzes which are appropriate
for workers in industrial enterprises but are not appropriate
Card 2/3 for students employed, for example, as travelling railroad

3-7-10/29
On Some PoSsibilities of Improving Technical Training in Correspondence
and Evering Courses.
workers.
Moreoverg students who do not comply with the requirements
of day courses, often take refuge in evening courses. As an
example the author mentions the evening courses of the Moscow
Transport Economics Institute where onlY 59 out of 720 students
are actual transport workers while 398 do not work at all. These
students reach the VIth year's course without any practical ex-
perience. As a result the institute often releases unqualified
specialists.
AVAIT--ABLE- Library cf Con-ress
Var d 5 /13

AUTHOR: Selishchev, V.I. SOV/3-58-11-11/38
TITLE-. The Form of Industrial Training is Changing (Menyayetsya
0 soderzhaniye proizvodstvennogo obucheniya)
PERIODICAL: Vestnik vysshey shkoly, 1958, Nr 11, PP 30 - 34 (USSR)
ABSTRAdT: In the near future, the number of higher school students
will be reinforced by youth having professional and engin-
eering skill. It will, therefore, not be necessary to be-
gin industrial training with the rudiments. This does not
mean that measures for improvement of industrial training
should be postponed until the reorganization of the second-
ary school is completed. These two processes should take
place simultaneously. The author sets forth his suggest-
ions for the improvement of the industrial training of those
students who have no experience. He begins with the on-
the-job-training workshops established at the vuzes where
the organization of work is poor. As an example of good
organization of practical training, the author mentions the
Moskovskiy institut inzhenerov zheleznodorozhnogo transports.
(Moscow Institute of RR Engineers) and those in Rostov and
Dnepropetrovsk, where the internal routine work has been
brought close to production conditions. He speaks of the
Card 112 advisability of replacing the pre-diploma practice in the

The Form of Industrial Training is Changing SOV/3-58-11-11/38
curricula by an obligatory 6 months' industrial practice be-
fore submitting the graduation thesis. A change in the form
of industrial Dractice is already taking place in such trans-
port vuzes as the Leningrad Institute of RR Engineers, where
72 % of the entire number of probationers are working inde-
pendently, and this is also the case at the Moscow, Tomsk,
Novosibirsk and Tashkent institutes. Practical work was
espe6ially well organized at the locomotive and car manu-
facturing plants. He also speaks of the difficulty of find-
ing plants where practical training could take place.
ASSOCTATION: GUUZ %linisterstva putey soobshcheniya SSSR (GUUZ,USSR Mi-
nistry of Transportation)
Gard 2/2

SELISHCHEV.- V. I" inzh.; LIDERS, G. V., dotsent
Track machinery station for student training. Put, i put. khoz.
6 no.9:25-26 162. (MIRA 15:10)
(Railroads-Track)
(Railroad engineering-Study and teaching)

L 23571-66 EVIT (d)/]~~P W /T/EWP(v) /'EWP(k)/V0 W/UP (1)
Aff IN _Rx -AP600*2600
SOWEE CODES uR/o286/65/boo/o23/oo95/bo95,,
AUTHORS: Selishchav, Ye. H Pashtayn-Sitnikov, N. V.: Volkernyuk, V. V.
ORG: none
TITLE: Distributive conveyer for automated lines. lass 61, No. 176825
/-announced by Special Construction and Technological Bureau for Design of Metal-
Cutting Tools and Equipment (Spetsiallnoye konsti;5ktorskoye I TleKnnolo CWWUYzr-
p--r-o-y-e-k-t-j-r-o-v-a-n-i-y-a-~-m-e-t-a-norezhushchego instramenta i oborudovaniya
SOURCE; Byulleten' izobreteniy i tovarnykh znakDv, no. 23., 1965., 95
TOPIC TAGS: conveying equipment,, automation equipment
ABSTRACT-. This Author Certificate presents a distributive conveyer for automated
lines. Endless closed chains are mounted in the frame of the conveyer and are
engraged -,jith drive and tension sprocket wheels. To simplify the design and to
increase the operation reliability with various technological handling processes,
one of the chains carries pin-shaped push-rods on its outer edge (see Fig. 1). A
chute with distributive ports for'outlet branches is mounted under the push-rods
in the frame of the conveyer. The ports are closed by double-armed spring-loaded
Card 1/3 ___UDC:__62.l.867.l5._ i

L 23571-66
ACC NR: AP60026oo
B-B
)iA
It- ZY
fit
b to
A-A
Fig. le 1 distributive conveyer; 2 end-I!,
less closed chains; 3 - drive sprocket
4 - tension sprocket wheel; 5 - pin-shaped
------ - push-rods; 6 - chute; 7 - ports; B.- out-
let branches; 9 - double-armed spring-loaded
interceptors- 10 - douji~e-armed spring-
loaded lever; U lever; 12 - axle; pawlj 14 - roller;
Card 2/3 15 axle

L 23571-66 -------
ACC NR: AP6002600
interceptors which are linked through a system of spring-loaded levers to pawl
axles fa3toned to the frameo During operation of the conveyer the pawls interact
with rollers placed an axles mounted between the chains in front of the corre-
sponding push-rodso Orig. art. bas: 1 diagram.
SUB CODE: 13/ SUBM DATEs 06Apr6h
Card 3/3

ATAtTASIU., Al., ing.; SELISCIII, N., ing.; LUPSE, T., ing.
Present problems relating to road maintenance. Rev transport
9 no.5:219-221 My 162.

SUISKkil 1(U711, ----
Mine-al resourceE of Algeria. Geogr obz 8 no. 3/4:100 lol,

S
Development of' machire printing in Yugosla,,da. r. 622.
TI-ILTIL. Vol. 4. No. 6, June 1955. Beograd.
," C UP C E :East European Accessions List (ILIAL), Library of rorr-ress,
Vol. !,, No. 12, December 1955-

G--intry
r
GDR G
:Organic Chemistry. Syntlaetic Organic Chemistry
Abs. Jour Ref Zhur - Kli'Am., No 5, 1959, No- 15317
Au:*, i~v) r 03ellsko, 0.; Schiibort, A.
I a 3 t _1 t t.1
T L L :On Sub3tancaq with Anti-E-Action. Report III.
Certain New Compaiind Ethers of Phenols
01~1r- Pub. :Ernaehrung3forschung, 1958, 3, No 2, 224-226
Ab 25 t r,, 'In continuation of studies begun earlier (re-
port II, see Ref 2hur-KbAm., 1958, 43281), a
series of compound ethers (CE) of phenols was
synthesf_zed. 35 9. of o-(I), m-(II) or p-cre-
sol, 12.5 g. of NaOH and 150 ml. of "A HaOH are
boiled for 30 minutes, the water is distilled
are slowly added,
off, 44 9- Of ClCH2COOC,H7
boiled for 15 minutes, 14 g. of NaOH in 150 ml.,
of water are added as rapidly as possible,
boiled for another 15 minlites, evaporated, and
115

G
t -Y
Ref 7-bar KUM,, N~) 5, 1*7~9, r%o. 15317
Title
C.- r
13 S t 1'a C t:2-, 3-, or 4-CH CH COOH (III) is PreciDi-
3061140 2
cont'd. tated by HCl, with a yield of more than 70%.
.L of I! and 8 g. of POC1 are
17 of 111, 11 9.
heated at 110-140 up to cessation of the Lpa-i,
ration of H01, cooled to 400, added to the ex-
cess of' the solution of NaHC03, and x-CH 3C6H40-1
GH2COOC.6FT4CH 3-Y (IV) (X = 3, y= 2) (jVa)'b.p.
1-15-1760/1 mm. are extracted with ether. Ana-
logously, other IV L.Oe obtained (x and y, tem-
215

Couatry G
C --- try
Abri. Jour flef Zhur Rhim-, NO 5, 1959, No. 1-5317
Au~ -:~ h -3
1AS t 1 i~! '.t
T L t
Or b.
Abst-r~tr:+.
cont'd.
:perat-ure of reaction, m.p. in OC. are iven):
2, 1~0-155, 56-57; 3, 2, 90-120, - ~b.p.
178 0 /1 mn. ); 3, 3, 130-140, - Co - P~ 194-
196~~i8 mm.); 3, 4, 110-120, 59-60; 4, 140-
150, 37-5-38-5 (b.~. i68-1700/1 mm. ); 4, 3, 1
135-140, 71-71.5; , 4, 130-140, 126-126-5. i
40 g. of CH CH-CHCOCl (V, VI acid) and 35 8.
of I are grLuaily heated to 1200,
cooled
and poured into a solution , and
of NaHC03
2 is extracted with ether,
CH3f"H=CHCOOC6H4CH3-
3/5

Juntl..7
a t -Y
'j'L' I
~~.bstract
1cont'd.
Bef Z4ur KLtm., No c, 195.~,,
a
11~'317
0
:b.p. 125-127 /12 rma. Analogously, from 22 g. of
V, CE of VI are obtained (original phenol, its
quanT,ityo in g., reaction temperature in OC.,
b,p. in G./mm. of corresponding CE of VI are
g ven); thymol, 30, 35-125, 118-120/4; carva-
col, 30, 25-125, 116-118/3; C5HllGOOC6H40CH3-2,
b.p. 1670/14 mm., is also obtained from 40 g.
of C5HjlCOCl and 35 9. of guaiaeol (VII) with
a reaction temperature from 50 to 140 0. 12 g.
4/5

33LISSNAYA, Ye.A.; OSTRAYA, S.S.
-4. lackheads and pimples in infants. Vest. derm. i ven. 33 no.2:
82-83 Mr-Ap 159. (MIRA 12:7)
1. Iz Nozhno-venerolot,icheskogo dispansera Moskvy.
(SKIN--DISUSIN)

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'so and-without wiling cWhing or br-Ming. [j is Wks& of
so a -mk 2w, starch 175, glycvrw IAO. petrulatm 60. " Ow
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r,43

SELI:3SKIY. A. B. Prof FA 4.1T65
USM/Madicine - Skin Diseases Jan 1948
Medicine - Penicillin
"Penicillin Ointment for Treating Skin Diseases,"
Prof A. B. Selisskiy, 3 PP
"Felldsher i Akusherka" No 1
Penicillin ointment Is very effective In coping with
pyococcus infection of the skin. In some instances
(furuncles, carbuncles, etc.) treatment required a
combined form, i.e., penicillin ointments on the
skin surface and penicillin injections.
-JW 41T65

Crl
USSR/Medicine - Penicillin
Medicine - Ointments
May/Jun 48
"The Effectiveness of Penicillin Ointments,
Depending on the Bass and Its Ingredients, "
Prof A. B. Selisakiy, G. Ya. Sharapova, B. M.
Lyebedyev, 3 PP
"Vest Venerol i Dermstol" No 3
Effectiveness of penicillin in ointments depends
on its base and ingredients. Penicillin in,vase.
line ointments has practically no bacteriostatic
effect against staphylococcue aureus (on pept6ne
agar). Activity of ointments on emulsion bases
1A higher. Ointments on anhydrous bases of
18/40,T79
IMP/Medicine Penicillin (Contd) May/Jun 48
stearin or wax with vazeline or vegetable oil
are effective. Glycerine used as an ointment
component does not affect penicillin.

jJ
LEEEDW, Ba Kep SELTSSKT-T$, A * Ba
Selebins a new preparation for treatment of sesma, Test, vener,
No. 4.9 July-Aug. 50. p. 41
1. Of the Skin Clinic (Head-Prof, L. N. Mashkillerson),, Central
Sldn-Verk3raologic4a Institute (Director-Candidate Kedioal Sciences
N. M. Twmnov) of the Kinistx7 ol'Public Health UM.
GUIL 19, 5, Nov., 1950

SELISSKIY,A.B.
[Treating sk.-".n diseases and prescribing for them; manual for
physicians] Lechenie zabolevanii kozhi i retseptura; spra-
vochnik dlia vrachei. Minsk, Izd.-vo Akademii nauk ESSR, 1955.
271 T) - (MLRA 8:11)
(SKIN--DISEASES)

SELISSKIY, A.B.
Cutaneous nerves in eczema. Arkh.pat. 17 no.1:68 -Ta-Hr '55
(ECZE14A, physiology, kMLHA b:10)
skin nerves)
(SKIN, innervation,
in eczema)

SELIS&KIY. A.B.
"fet.--t
[Skin diseases in children and adolescents] Bolezni kozhi u detei
i podrostkov. Minsk, Izd-vo Akademii nauk BSSR, 1957. 269 p.
(SKIN--DISEASES) (MIRA 10:7)

SELISSKIY, Aleksandr Borisovich
[Manual on skin diseases; clinical aspects and treatment of skin
diseases, prescription writing. homeotherapyl Spravochnik po
ko2hnym bolemiam; klinika i lechenie zabolevanii kozhi, retseptu-
ra, gomeoterapiia. Minsk, Gos.iza-vo BSSR, 1959. 410 p.
(SKIN--DISEASES) (MIRA 13:9)

SELISSKIY, A.D.
DgrmabrasiDn; survey of the literatm-e. -Vest.derm.i von. 34
no.10935-39 160. (SKI14-SURGERY) (MIRA 13tll)

.SELISSKIY, Aleksandr Borisovich, prof.; PAVLOV, N.F., dots., red.;
- -- ZAYTSLTk,-l -., -r--e-d-.iiQ--va; VOLOKHANOVICH, I . , tekhn. red.
[A guide to skin diseases; clinical aspects and treatment of
diseases o' the skin, pharmacotherapy and prescription fil-
ling] Spra-iochnik po kozhrVm bolezniam; klinika i lechenie za-
bolevanii '-/
roporto of Mi biLor-raz Conference on
Relaxation Phenomena in Pure Metals and Alloys SOV-3-58-9-25/36
"~~-4 Apr l'bacow Iqst. of Steels.
.Institute) covered the reailient reaction of spring alloys,
various physical and technological effects on it and the
methods of its measurement. Ya.P. Seliaskiy (Institute of
Precision Alloys TsNIIChM) toir-of-s-ulb-s-M-~g- oscillations
of ultrasonic frequency in some ferromagnetic solid solutions.
R.I. Garber and A.I. Kovalev (Physico-Technical Institute
UkrSSR AS in Khar1kov) spoke of the temperature dependency
of moduli of elasticity of iron.
VeSt. V~VRS'ne qhkOIT-, 0, '70_71, lc-'C'
(FiLnizov' Yu. V.

r__
PHASE I BOOK EXPLOrTATTO14 SOV/3528
mo3cow. Dom nauchno-tekhnicheakoY propaeandy
rr"c-.en1y* tLl*trazvukt V proMyahlenmoatl~ abornik atatay (In-
duatria.1 Use OZ =tr9-aund; Collection Of Articles) Moscow,
masingiz, 1959. 301 p. 8,000 p,inted,
Sponsoring Agency: Obsbchaatvo po raSprostranenlyu politishooxW~
I nAuchnykh %manly RSPSH.
Ed (Title pags)s V.P. Nozdrev, Doctor of Physical and Mathematic
iciences, Professor; Ed. (Inside book): O.P. Kochatova, Englneo!~
Tech. Zd,t V D ZlIkind, Managing FA. Car LiteraCure an Machinery
and tratrtanon; iLlnufacturing (KAahglz); N.V. Pakrovskly, Engineer.
PURPOSE; This book Is Intended for engineer* and technicians engaged
In the application or ultrasonic$ In machinery manufacture and In
other branches or industry.
COYMAGEt This to a collection of papers read at the first &II-
Unlon conforonce on the Lisa of altraaonios In industry, Attention
is focused mainly an the dezzription of uItra2onic'arquI7pn:ont and
an the "a of ultrasound tar the machiming a., hard materials and
tar flaw detection. The effect of ultrasound on metal-ary*talla-
tion processes is Lisa discussed. No personalities are mentioned.
Referancesaccompa,y many_o r the papers.
Kitayzqrodskl.y,._Yu..T. En-ineer; and M.g_._Kop
,an, Candidate of
-fachnIcal Sclncos. bltriaonI4 Equip:3ent for 1,~,Iuatrial Applica.
tions 64
Markov';_A7.I_.,_Cjndldate of Technical 3cience.1, Docent. Design
_1AZ_COn3t_ructiOn Of Vibrator& tar Ultrasomic Machining 77
Bulychava, I.H., Candidate of Technical Sclenzes; Ta-T-UkIrvich,
-cabdIdate al-Technio&I 3cidjo.3; and..Ya_p. -q.11sakly. Candidito
or TectuAcal Sciences. Magnetic Alloys for_UltrauoTi~o Applies-
tiona 91.
Makarov, L.O.. Engineer. Methods of Making D,!slan Calculations
_f_0_r_Pdr-Ty~i' Exponential Ultrasonic Concentrators 102
Golya.mina, L.P. U36 Of FOrrit.-O as Ultraoonlc-Wa~e Radiators 115
Sem*mnikOv, Yu-B., -EnZinear. Method of TransroraIna Input Basis-
-tance-of a T-;Ilar Radiator 125
Sir0tyuk X 0 Engineer. Matching a Ocnarator of Electric
_05CIlliLtIani iith a quartz' RbAiator DirvcUy cc~_L~d with th6
Generator Circuit 129
LZNzI_a.r_8.N; --r- Enal near. Characteristics or the Ultrasonic Muchin-
IAF or vet&la 136
piG&rav5kiY-_~.-M., Candidate or Technical Sol.nceal anA_~,A.
Oalned at thetAnlnZrA4skiy Fetelli-chasay
zav0d nIngrad Kctal-product3 P ant) In the Ultrasonic
Drilling of HjIoa In Quartz Plates 146
Doctor of Tichnical Sciences, Professor; Xu,_
44- KlzrOk4l, Enjineer; 1,14 V.O. Averlyanova. SOJad FroblaMa In tit,
'UMr~1hAd'1FC__ftchlning of x~ tj-rrjrd----- - 149
TaLunin, Idate Of F-1yalcal and M&tha-,,%tjc%l Sciences.
tMet tie Vibrations on the CryBtnllj~btjoh anj proc&aalrLg
properties or Alloys 163
Bagdaaarov, Kh,S,, Candidate Of Chemical Sciences. Erfect or
Ultrasonic Vibrations on the Process of CrystAllization 175
or Technical Sciences. Ultrasonic
MW batacttan 16~,
Y0rmOI9_Y_._I.N_ Engineer. Ultrasonic Instruments Developed by
TsNlfl~iiish for ty'91 Measurement or ThIckneov anj Product Control 211
_QMbanov~, M,R., Candidate of Technical Sciences. Ultrasonic Do-
tectf6i~ 0_CFI&ws In Massive Waldo 223
Y Inspection of Cabe Depth In Electrically
Steel Produota 240
Babkin, N,V.-Enginear. Design or piezoelectric Tranoduaera tor
'Ultrasonic Fla. Detectors 253

JUTRORSt krtsishavokly, N.A., Vasillywv. r ..... %--h*lyayev, 11-y-
&Ad bolivBkly'
-----------
VITIRI fte Xffeat of Douteron-Bombardmont on X146trIcal Roslatozoo
of the OrdurLag Alloys N13P*, Yo3A1 and the Agoing Alloy
to-11-TI (Daystv&14 banbardirovIci daytron&ai na olaktra-
soprotivIonlym upor7zdcahlvayUshQhlkn.TW aplavoT Mtge,
Fv.'kI i staroyushebego splava Fe-Mi-Ti)
PIRICOMAW Flalka **tallow I Xetallovodoniy4, 1959, Val 7, Ir 1,
pp 53-56 (Usaft)
A53TRACTs Tho author* studied the *treat of irradiation with 4 MoV
deuterons on electrical resistance of the ardoring 421010
2 FoAl and the ageing alloy with 36% ML, 4.5% TI and
'
-
thlolmoss union
2
o
a
"
at 'Vs. .3ort
re
ZY
y
'du
aN
toma
tti
l
mr:
of
ce a
a
.
v
ith
r
.
e
n
o
I
c
assured Interact
throughout the whole Momple. Bator* measurement. o"plos
were subjected to varlou* form& of beat troat~ant. The
ordered state of the Ii are alloy was obtainoil by slow
Card 2/4 scaling for a fortnight :roa 650*0. ?be 703A1 alloy was
ordered by cooling at the rate of 25OC/hour from 550-abo0o.
The aloordered states of theoiji3pa, y03AI alloys war% pro-
du4od by quenching from abo C. &9&"n9 of thm ?"I-Ti A1107
was O'chisv0d by rOur-hOur hooting of cold-defor"d o"plos at
700*
~g. The letter 41107 was also tested after quenching from
LOW Q. For irradiation the samples were placed In a caasstte
sooled by ro"LA t r The deuteron current density did
not exceed ;.d the tun orator* or the s"ple during
irradiation did not rise above 'ago . Ylectrical real.tLav*
"ma measured by means of a potentiometer before and after
irradiation. The romults are shown in Tables 1-3. LrrAdistiox
increased, in general, the electrical rovistanoo of tjoo
"Wooled fordored) Y#_," and decreased LbAt or too quenched
F*3LI- the ol*otrloal r*sletanc* or both the quenched ad
thi unhealed (Ordered) XIP. fell With Increant of the
t!ral domo.r4asivod. I;Qw intAnaLtles of irradiation,
lAte
up 6 x 101D douterona/ext2s decreased the electrical
"&'Stand* of both 103" and Xi3F*- 14 the seem Of the
Card 2/4 P~0-81-Ti 41107 the Ah-0965 On irradiation were hardly
largor than the experimental error, but their alga see-
Positive in. quenched samples and asgLtiv* in aged saxpl.s'
The authors conclude that deuteron bombardment produces
further ordering of the XL3F9 &U07. rz the p63AI alloy
deuteron irradiation produces & state intermediate between
the disordered and ordered states. AStor IrradiAtion the
samples more subjected to tempering at various temperatures.
In the Gass Of F&AI the shape Of the *100trIcal r*ol.temo.
OUrTes (PI9.1) at Irradiated samples, FbIch were subsequently
tempered at 25000, contir..d that deuteron irradiation does
1A fast produce in intermediate state or OrdorlAg. Womn
the irradiated 113ye samples war* tempered the durations
Or tempering worm insufficient to reach a tat$ of equilibrium
(Pig.2). go noticeable difference was observed between the
behaviour of Irradiated and the Rou-Irradlated FG-Ai-Tl
:amplo; aft:r.t mp:x-lng. There are 2 figuxes, 3 tables and
Card 3/4 ansi sh r f r:uc a.
A3=UTIQXs lostitut protaisloncykb opjaway TgMllChX (Institute of
Precision Alloys TaIlICbM); 2-y nauch4o-ipalodov4t*l-&xjy
tlzLcb0dkly JA-t IIGU (Second 30l*Rtlfla-8ooo&rah physics
Z"tltut*. X4640w State University).
ALIBUT"WI Key 27, 1957

2,'-r(2.), 18(3), 18M SOV/126-7-2-9/39
AUTHORS: Borodkina, 11. M., Detlaf, Ye. I. and Selisskiy,Ya.P.
'j:ITLE: Recovery and Recrystallisation in the Ordering Alloys
Fe-Co (Vozvrat i rekristallizatsiya v uporyadochiva-
yushchikhsya splavakh Fe-Co)'
PERIODICAL: Fizika Metallov i Uetalloved-eniye, 1959, Vol 7, Nr 2,
pp 214-224 + 1 plate (USSR)
ABSTRACT: The results of an investigation carried out with the
aim of elucidating the characteristics of recovery
of the initial statue of recrystallisation of Fe-Co
alloys in relation to cobalt content are described
in this paper. Alloys, the compositions of which are
shown in Table 1, were cast from Arinco iron and
cobalt 6-1 into ingots weighing 1 kg. These were forged
at 1180 C info billets and subsequently rolled at
1100 to 1150 C into strip of 3 mm thicImess. The
cut into
which
hot rolled strip
gas
quenched from 900 C and cold rolled to thicknesses of
0.5 and 0.1 mm. Square specimens 20 x 20 mm were
cut from the cold rolled strip. These were sealed in
evacuated quartz ampules and annealed at temDeratures
Card 1/6 of: 150, 300, 400, 450, 500, 5500, 600, ?00 and 750'JC,
were water
squares

SOV/126-7-2-011/39
Recovery and Recrystallisation in the 0_-d_-r_4r_'- Alloys Fe-CO
at which they were soaked for 5, 10 and 15 mins, 1 and
2 hours. In special cases the soaking; time was 8 hours.
Cooling was carried out in air. Specimens of 0.5 mm
thickness were used for hardness tests on a Vickers
machine using a load of 5 kg and for an X-ray investi-
gation in a RKE camera for rapid exposure (Ref 2) and
in a KROS camera. Exposure in this case was carried
out in a Co irradiation, both the adaptor and the
specimen were rotated. The distances between the
object and the film was 100 mm. In the X-ray photo-
graphs the K -doublet lines from. the plane (013) were
visible whic9 in the case of deformed-specimens appeared
diffuse and merged into the back-round of the X-ray
picture. kn increase in Co content of Fe-Oo alloys
above 251% is associated with a decrease in lattice
parameter (Ref 3), as a result of which the doublet of
(013) shifts in the direc8ion of large Bra-g angles -
0
for a 25016 Co alloy 81 7 for a 750/6 Co alloy Pd= 860
For this reason the sensitivity of the method to
change in line width was great and increased -aith
Card 2/6 increasing Co content. In order to estimate the
C~

sov/126-7-2-9/39
Recovery and Recrystallisation in the Ordering Alloys Fe-Co
changes in width and intensity of the doublet line
durin-, annealing, the X-ray films were photometered
in the micro-photometer LIF-4. The beginning of
recrystallisation was indicated by the appearance of
separate interference spots in the doublet line on
exposure to the KROS camera with a ri--id specimen
and adaptor. Besides9 specimens of 0.1 mm thickness
were investi;~-ated in a Mo irradiation in a camera
with a flat adaptor in order to obtain textural
X-ray pictures at an object-film distance of 60 mm.
Here the interference rings of the (011), (002) and
(112) planes were clearly apparent, from which the
nature of the texture obtained could be established
and the progress of recrystallisation 3ould be seen.
In Fig 1 the annealing temperature and ainim,.= soaking
time reauired for the appearance of the maxima K and
~_ al
KU2 in the photometric curve is shown in relation
to the Co content of the alloy. Fig 2 shows micro-
photometric curves for alloys with different Co content
t J_
which have been annealed at 400 C for 30 mins, FiEs 3
Card 3/6 and 4 show micro-Dhotometric curves for 650% Co and

SOV/126-7-2-9/39
Recovery and Recrystallisation in the Ordering Alloys Fe-Co
35% Co alloys respectively which had been annealed at
various temperatures and for various soakinn- times.
Fig 5 shows micro-photometric curves for a 42% Co alloy
which had been annealed. at various temperatures for
2 hours. PiS 6 shows the temperature ranges of
recovery and recrystallisation of alloys with differinG
Co contents: I - Kai and K a2 maxima; II - sharp K al a-ad
Kag maxima; III-appeartu-ice of separate interference
SD 'us in the rin6,; IV - complete disappearance of the
continuity of the rinb-. The region of supplementary
diffuseness of the interference lines is indicated by
brackets. On the basis of their experiments, the
authors arrived at the follo-wing conclusions:
1) A relationship between the temperature range of
C3
recoverl, and the composition of the Fe-Co alloys
a
investigated has been established. The begirring. of
the breakini~ up of the Kcc doublet in X-ray photoeraphs,
characterising the initial sta,-,~;e of recovery, is
observed at very low temperatures in alloys of the
Card 4/6 stoichiometric compositions Fe 3C0 , FeCo and FeCo3. This

SOV/126-7-2-9/39
Recovery and Recrystallisation ix- the Ordering Alloys Fe-Co
is due to the fact that In a number-of solid solutions,
the ordering alloys after deformation are thermo-
d~namically least stable,
2 All cold deformed Fe-Co alloys containing between
25 and 7_5% Co can harden on low temperature annealing.
The hardening takes place at annealing temperatures
which are not high enough to give a broken up doublet.
This hardness is due to ordering in the non-uniformly
stressed lattice and formation of mixed regions of a
different degree of ordering, In spite of some increase
in stress in the distortion of the lattice at various
intervals of the ordering process which brings about
0 0
hardening, the process on the whole must lead to a
decrease in free energy.
3) In alloys containing 35 and LL20166 Co the repeated
diffuseness of the doublet c--incides in temperature
with a retardation in the fall of hardness after
attaining a maximum in hardness-annealing temperature
curves (35016 Co) or even with the appearance of a second
Card 5/6 maximum (42% Co). The effect described takes place in
the transformation ranGe which i,.,as found by Masumoto,

SOV/126-7-2-0/7,q
.1i - ,
Recovery and Recrystallisation in the Ordering Alloys Fe-Co
Saito and Shinozaki (Ref 4) by means of zhermial
capacity measurements,
4) Recrystallisation in the orderin.z-- Fe-Co alloys
commences at order-disorder transformation temperatures,
Recrystallisation commences at the highest temperature
in an alloy of the stoichiometric COMDOsition FeCo.,
There are 9 figures, 2 tables and 6 references, 2 of
which are Soviet, 4 English.
ASSOCIATION: Institut pretsizionnykh splavov TsNIIChM
(Institute of Precision Alloys TsNIIChU)
SUBMITTED: 1,1ay 14, 1957
Card 6/6

SOV/126-7-4-7/26
AUTHOR: Selisskiy, Ya.P..
TITLE: On the Evidence of' the Transformation in the F e3 Al
Alloy being a Second-Order Phase Change
PERIODICAL:Fizika metallov i metallovedeniye, 1959, Vol 7, Nr 4,
PP 534-543 (USSR)
ABSTRACT: It has been proved by Rhines et al (Ref 1 and 2) that
the order,-,,-_-2,disorder transformations in alloys whose
composition is given by the formulae Cu3Au and CuAu are,
in fact, classical phase transformations, i.e. first-
order phase changes. These findings, however, do not
C3
necessarily apply to all alloys in which the order
disorder transformation occur and the object of the
investigi~tion described in the present paper was to
determine the character of the transformation taking
place in the Fe3AI alloy. X-ray and dilatometric
measurements were used for this purpose, the experimental
alloy containing (in weight %) 13.2 Al, 0.07 Mn,
0.11 Si, 0.025 C, the remainder Fe. The dilatometer
specimens (50 mm long, 3 mm diameter) were machined from
6 mm diameter rods obtained by hot forging the cast
Card 1/11 ingots and annealed (in hydrogen) at 11000C for 3 hours.

SOV/126-7-4-7/26
On the Evidence of the Transformation in the Fe3Al Alloy being a
Second-Order Phase Change
The same rods were used for the preparation of filings
used for the X-ray analysis. (The particle size of the
filings used in the experiments did not exceed 5.lo-3mm.)
Heat treatment of the X-ray specimens was carried out in
a vacuum quenching furnace shown schematically in Fig 1.
The filings were contained in a small quartz boat (1)
which was suspended inside a quartz tube (2) on nichrome
wires (3) attached to a permalloy, arc-shaped anchor (4).
On the completion of the heat treatment, the permalloy
anchor (4) was lifted from its holder (_5) with the aid of
a magnet, and the quartz boat with the filings was dropped
into the quenching tank (6). Oil D-2 (used generally in
diffusion pumps and characcerized by low vapour pressure)
was used as the quenching medium. No sintering of the
iron-aluminium filings heat tr-eated in vacuum of 5.10-4mm
Hg occurred at the highest temperature employed (850%).
On falling into the quenching oil, the filings formed a
suspension; this ensured that all particles were cooled
at sufficiently fast and uniform rates. In the first
Card 2/11 series of experiments all X-ray specimens were heated to

SOV/126-7-4-7/26
on the Evidence of the Transformation in the Fe3Al Alloy being a
Second-Order Phase Change
7000C, held at this temperature for 1 hour and then
heated or cooled to the quencIiing temperature. The heat
treating cycles are listed in column 1 of Table 1; the
numbers following the temperatures denote the holding
time (in hours, except the first cycle where the holding
time at 6000C was 20 min) at the temperature; the last
temperature in each cycle is that from which the X-ray
speciazen was quenched. The second column gives the
values of the lattice parameter, a, of the corresponding
specimens. The symbols I(Ill), and 1(2,Q) in the
expression the values of which are listed in column 3,
denote the intensities of lines (111)a of the super-
structure of the Fe3Al alloy and lines (220) of the
normal crystal lattice. The values of S lisied in the
last column of Table 1 were calculated from the data
listed in column 3 using the formula at the bottom of
P 537; these values give the relative measure of the
degree of the long-range order at various temperatures.
,rhe temperature dependence of the lattice parameter of
Card 3/11 Fe3AI (plotted from the data in Table 1) is snown

SOV/126-7-4-7/26
On t1ile rvidence of the Transformation in the Fe3Al Alloy being a
Second-irder Phase Change
graphically in Fig 2a. The rate at which the lattice
parameter attains the equilibrium value is characterized
by data given in Table 2. The heat treating cycles are
given in column 1: all specimens were heated to 7500C
and held at this temperature for 2 hours; the first
4 specimens were then cooled in 10 min to 4100C and
quenched immediately or after 1, 4 and 7.5 hours' holding
at this temperature; the last 4 specimens were cooled
in 15 min to 3500C and then quenched immediately or
after 1, 2.5 and 3 hours at this temperature. In the
next stage of the investigation the order-disorder
transformation was studied by means of dilatometric
measurements, in irhich two series of specimens were used.
All the specimens in tne first series were subjected to
the same preliminary heat treatment which consisted of
2 hours at 7500C followed by 30 min at 800*C and quenching
in water. The dilatometric measurements were taken
during both the heating and cooling cycles, the rate of
heating being 300*C per hour; for the cooling cycle
Card 4/11 the dilatometer heater was switched off. The typical

soV/126-7-4-7/26
On the Evidence of the Transformatioii 'rl t'lle F'e3AI Alloy bein- a
0
Second-Order Phase Change
results of these measurements are reproduced in Fig 2b
in the form of differentiai dilatometer curves sitiosfing
the difference (in mm) between tl-ie expansion or
contraction of the investigated specimen and that of
a standard specimen in whicli no sol-id state transformation
took place. From the data reproduced in Fig 2b the
temperature dependence of the coefficients of thermal
expansion was plotted (10-6/0C versus OC) for both the
investigated and standard specimen (Fig 2v, curves I arid
2 respectively). The dilatometer specimens of the second
series were all quenched from different temperatures,
having been first heated to 7000C and held at this
temperature for 2 hours; while being cooled to its
quenching temperature, each specimen was subjected to
one or more (depending on the quenching temperature)
isothermal treatinents (each of 2 hours duration) at the
following temperatures: 550, 500, 450, 350, 300 and 2500C.
During the dilatometric, measurei,.tents these specimens
were heated at a rate of 2000C/h; on cooling, the
Card 5/11 specimens were held for one hour at each of the following

SOV/126-7-4-7/26
On the Evidence of the Transformation in the Fe A13AIloy being a
Second-Order Phase Change
temVeratures: 700, 550, 500, 450, 400, 350, 300 and
250 C; the rate of cooling between each of these
temperatures was not faster than 50C/min. The
dilatometer curves of the specimens of the second
series, quenched at 700, 550, 500, 450, 4oo, 350, 300
and 250.C are shown in Fig 3a, b, v, g, d, e, zli and z
respectively. It was observed in the course of these
experiments that on cooling, when the specimens were
held at constant temperatures, the dilatometer reading
was also constant which indicated that the volume
chariges occurring in the specimens due to the disorder-
order transformation took place rapidly and that the
state of equilibrium was already attained at the
beginning of each isothermal treatment. The dilato-
meter curves of the sFecimen quenched from 700*C (Fig 3a)
are similar to those shown in Fig 2b. Regarding the
curves of other specimens, quenched from progressively
lower temperatures, it will be seen that the lower the
quenching temperature, the less pronounced is the
Card 6/11 minimum on the heating part of the dilatometer curve;

SOV/126-7-4-7/26
(~n the Evidence of the Transformation in the Fe Al Alloy being a
Second-Order Phase Chauge 3
this is associated with tile fact that the lower the
quenching temperature, the higher was the degree of tile
long range order- irl. a given specimen at the beginning of
tile experiizient. This effect is shown also by the
variation of tile coeft'icients of thermal expansion
calculated from tile heating parts of tile dilatometer
curves in Fig 3, for three temperatures - 250, 275 and
300OC; tile relationship between the expansion
coefficients and the quenching temperature is shown in
Fig 4. It will be seen that while the expansion
coefficient of specimens quenched from 7000C is quite
small (becoming negative at 2750C as a result of the
large volume ciiange due to ordering), it becomes larger
as the quelichin �. temperature decreases; specimens quenched
from 250 to 400 C have the expansion coefficients
practically the same at the three selected temperatures.
The various temperatures indicated in Fig 2 and 3 are
given the following interpretation: Tj = 1800C is the
beginning of the tion-linear expansion of the (quenched
Card 7/11 i.e. disordered) alloy on heating and of tile decrease of

SOV/126-7-4-7/26
On the Evidence of tile Transformation in the Fe3AI Alloy being. a
Second-Order Phase Change
the expansion coeffici exit; T2 = 2600C marks the
beginning of rapid contraction of the alloy on heating
and the change of' tile si_-n of the expansion coefficient
from positive to negative; TpH = 2700C is the
temperature at which the order-disorder transformation
begins in the heated alloy; T3 = 280% marks the end
of rapid contraction of the heated alloy and the change
of the sign of the expansion coefficient from negative
to positive; T4 = 3700C is the temperature at which
both the standard and the investigated specimens have
the same thermal expansion coefficients; TKNI - 5450C
marks a deflection on the heating portion of the
dilometer curve, a sharp maximum on the graph of the
temperature dependence of the expansion coefficient and
disappearance of the long range order; T. = 61o to 6150C
marks tile magnetic transformation; Tffl - deflection
point on the cooling portion of the di atometer curve
whose position depends on the rate of cooling and which
indicates 0the appearance of the long range order;
Card 8/11 Ty, = 300 C marks the beginning of the linear contraction

SOV/126-7-4-7/26
On the Evidence of the Transformation in the fe3Al Alloy being a
Second-Order Phase Change
of the alloy during cooling. Thus, when the Fe3Al alloy
in which the disordered structure has been retained by
quenching is iieated, the disorder-order transformation
begins at a comparatively low temperature (TI = 160 0C)
and takes place within a comparatively narrow
t~~mj)eratttre range (180-Z700C) while the order-disorder
change occurs (on licating) within a wider temperature
rarige (270-5450C). The disorder-order transformation in
a specim2ri cooled from high temperature occurs between
345 and 3000C. The values of the lattice parameter (a)
measured in the 550-2509C temperature interval (see
Table 1) were used for the determination of' the value of
relative compression, 6a/eia, brought about by the
disorder-order transformation. (tia is the total
reduction of the lattice parameter of' alloy cooled slowly
between 55C and 2500C; 6a i5 the reduction of the
lattice parameter cooled slowly from 5500C to a given
quenching temperature.) The relationship between 6a/jNa
and T/Tk (where T is the absolute quenching temperature
and Tk corresponds to absolute Tykll) is shown it, Fig 5,
Card 9/11 both for the Fe3AI alloy (curve 1) and for the Cu3Au

SOV/126-7-4-7/26
On the Evidence of the Transformation in the Fe3A1 Alloy being a
Second-Order 1hase Change
alloy (curve 3). Curve 2 in Fig 5 represents the
variation of S (the magnitude of which is proportional
to the degree of the long range order) with T/Tk-
lt will be seen that while there is a sudden change of
volume of the Cu3Au alloy at tkie Kurnakov point (Trt,_L),
Uiis being one of the characteristics of a first-oi-der
p1liase c1hange, the volume of the Fe3A1 alloy changes
monotonically. The divergence between the S and 6a/aa
curves for the Fe3A1 alloy is attributed to -the fact
that, according to Owen and MacArthur (Ref W, the volume
changes are associated with the initial stages of the
disorder-order transformation and take pla,~e in a short
time interval, while the variation of the intensity of
the superlattice lines is associated with the growth of
the anti-phase domains which is a slower process. It is
stated in the concluding remarks that the absence of
any discontinuities in the variation of the studied
properties of' ttie Fe3Al alloy during the disorder;~grder
transfo.rmation, taken in conjunction with other published
Card 10/11. data, is a convincing proof that this transformation is a

SOV/126-7-4-7/26
On the Evidence of tile Transformation in the Fe3Al Allo-y being a
Second-Order Phase Changge
second-order I.kiase ciiange. There are 5 figures,
2 tables alid 10 roferences, 9 of w1hich are EnglisLl and
I :3oviet.
A660CIATION:Iiistitut pretsiziomiy1cla splavov Tsentrall-nogo nauclino-
issledova'uellskogo instituta chernoy metallurgii
(Tile Precision Alloys Institute of tile Central Ferrous
Netaliur.,,,y Rese.-irch Institute)
SUBMITTED: Julie 11, 1957
Card 11/11

A'UTIIC:RS: Ravdell, M.P. and Selisskiy, Ya. P. SOV/126-7-6-13/2/t
TITLE: Investigation of Transformations in Alloyed Permalloy
PERIODICAL: Fizika metallov i metallovedeniye, 1959, Vol 7, Nr 6,
pp 885-892 (USSR)
ABSTRACT: The authors have carried out a systematic investigation
of hardening of Ni-Fe-base alloys. The alloying elements
used were Mo, Cr,' Cu, V, W, Si and Mn and were added
to the Ni Fe alloy at the expense of iron. The chemical
compositiL of the alloys investigated is shown in a
table, p 886. The alloys were melted in a high-fr-equency
induction fim7-mce and cast into ingots of 5 kg, homogenized
in hydrogen at 11000C and subsequently forged partly into
billets and partly into rods of 8-9 mm Specimens for
dilatometric and thermomagnetic study i-e = 50 mm, d = 3 mm
and 4 = P-5 1-11ml d = 3 mm, respectively) and wire of 1 mm
diameter were produced from the rods. All electrical
resistance measurements were carried out at room tempera-
ture on specimens of I mm diameter by a potentiometric
method. The dilatometric study was carried out on a
differential dilatometer of the Shevenar type which was
Card 1/5 provided with a special device to enable isothermal soaking

SOV/126-7-6-13/24
T.tivestigation of Transformations in Alloyed Permalloy
to be carried out. The thermomagnetic study was carried
out on an Akulov system anizometer. All specimens of the
alloys investigated were subjected to stepwise heat
treatment (heating to 9000C followed by stepwise cooling,
with lengthy soaking at the following temperatures:
550, 500, 450, 400, 350, 300 and 2500C). After soaking,
the duration of which varied between 24 and 120 hours
depending on temperature, the specimens were immediately
quenched in water. Such heat treatment ensured different
degrees of order in the specimens in relation to the
temperature of quenching. In Fig I the change in
electrical resistance of a specimen quenched from 900*C
in relation to the quenching temperature is shown.
In Fig 2 dilatoinetric heating and cooling curves of a
non-alloyed Ni-Fe alloy, converted to the ordered state
by stepwise heRt treatment, are shown. In Fig 3 curves
are plotted for the dependence of thermal expansion on
temperature. Fig 4 shows the change in volume of alloyed
Fe-Ni alloys during isothermal tempering in the dilatometer
Card 2/5 furnace. The tempering temperature was 4500C and the soaking
time 5 hours. Fig 5 shows thermomagnetic heating and

SOV/126-7-6-13/24
Inves.tigation of Transformations in Alloyed Permalloy
cooling curves. In Fig 6 similar curves are shown for
the alloy Ni (Fe,V), containing 4% V. The authors arrive
at the folloaing conclusions: the introduction of 3% Mn
at the expense of iron brings about a considerable
intensification of ordering effects in a Ni Fe alloy.
This is shown by a considerably increased dKp in the
electrical resistance after stepwise heat treatment. A
greater volume effect can be observed in this alloy than
in the selected one during disordering and isothermal
tempering. The order-disorder transformation temperature
of this alloy is higher than that of the Ni Fe alloy.
The magnetic saturation of -the ordered Ni (Pe,Mn) alloy
is considerably greater than that of the Ri Fe alloy,
whereas Mn lowers the magnetic saturation o~ a disordered
Ni Fe alloy. Such peculiar influence of Mn is due to
th~ structure of its 3d-shell. Other solid solutions,
which also contain Mn, become ferromagnetic after
ordering. It appears that Mn in the ordered lattice also
participates in a magnetic reaction, as a result of which
agnetic saturation increases strongly. A supplementary
Card 3/5 'fall in electrical resistance on tempering is associated

SOV/126-7-6-13/24
Investigation of Transformations in Alloyed Permalloy
with an increase in saturation of the ordered alloy
Ni (Fe,Mn). Copper brings about a concentration
di;order in "he Ni Fe alloy. Additions of Cr, W and V
act on the orderini process of the Ni Fe alloy in the
same way as Mo (Ref 3), changing the Aature of the effects.
An anomaly in electrical resistance has been found to
exist in Mo permalloy as well as in alloys containing Cr,
V and W, i.e. an increase in the electrical resistance
after heat treatment in the temperature range at which order-
ing takes place. All these alloys exhibit identical
dilatometric and thermomagnetic anomalies. No lattice
contraction, characteristic for the ordered state, occurs
in these alloys. Also there is no sharp volume increase
on disorder establishment. The dilatometric peculiarities
of these alloys are characterized only by a change in the
thermal expansion coefficient at the transformation
temperature. In all these alloys a temperature range is
observed for the ferromagnetic transformation instead of a
sharply defined Curie point. Such an effect of Mo, Cr,
W and V is due to the fact that complexes are formed in a
Card 4/5 one-phase solid solution at definite temperatureA the

SOV/126-7-6-13/24
Investigation of Transformations in Alloyed Permalloy
Curie Pointsof which differs from that of the basic solid
solution. This can be seen even more convincingly in
alloys containing ' Si which forms very stable complexes.
There are 6 figures, 1 table and 8 references, 1 of which
is Soviet, 2 English, 3 German and 2 French.
ASSOCIATION: TsNIIChM
SUBMITTED: May 15, 1957 (Initially)
June 9, 1958 (After revision)
Card 5/5

361j4, '
S/137/62/000/003/105/191
A06O/A1Ol
AUTHORS: Artsishevskiy, M. A., Vasil'yev, S. S., Koshelyayev, G. V.,
Se _P. -
TITLE: Action of deuteron irradiation upon the electric resistance of
alloys undergoing ordering and aging-
PERIODICAL: Referativnyy zhurnal, Metallurgiya, no. 3,1962, 6, abstract 3138
("Sb. tr. Tsentr. n.-i. In-t chernoy metallurgii", 1959, no. 22,
168-176)
TEXT: The effect of deuteron irradiation upon the electric resistance R
of alloys N'3Fe, Fe3Al undergoing ordering and of an alloy of Fe with 35% Ni
and 4.5% Ti undergoing aging was investigated. The specimens were irradiated in
a cyclotron with deuterons having an energy of 4 Mev. The thickness of the
specimens constituted 20 - 30,1,--. The R measurement was carried out by the
potentiometric method, Becau~e of the small dimensions of the specimens the
voltage and the current leads constituted a single whole with the working part.
The specimens of N13Fe and of Fe3Al were Investigated in the ordered and the
unordered states; the specimens of Fe-Ni-Ti - in the aged and hardened states.
Card 1/2

S/137/62/ooo/oo3/lo5/19l
Action of deuteron irradiation ... A060/AlOl
It was established that when the ordered Fe3AI alloy is irradiated its R is
increased considerably, and the R of the hardened alloy - drops. The bombarding
of the N13Fe alloy in the ordered and unordered states causes a considerable
decrease in R. In all cases irradiation In fluxes up to 5 . 1017 deuterons per
1 CM2 causes a sharp change in R, at a further increase of the total flux the
rate of change of R drops. The effects uncovered in the Fe-Ni-Ti alloy do not
exceed the limits of experimental errors. It is considered that the most
probable process causing the reduction in R is the ordering. A considerable
drop in the R of the alloy Ni~Fe is noted, whose degree of ordering corresponds
to a temperature of 250 - '300 C. In this alloy a further occurrence of ordering
under irradiation is possible. The shape of the R curves of the irradiated
specimens tempered at 2500C confirms the hypothesis as to the attainment of an
intermediate degree of ordering as result of the irradiation. In tempering the
Ni3Fe the soaking time of the specimens at the respective temperatures was in-
sufficient to obtain an equilibrium. The character of the R variation of an
irradiated unordered specimen is close to the R variation of an unirradiated
ordered specimen. In tempering the Fe-Ni-Ti alloy no great difference in the
behavior of irradiated and unirradiated specimens was discovered.
[Abstracter's note: Complete translation] A. Rusalkov
Card 2/2

24 (2), 24 (6)
AUTHORS: Borodkina, M. M., Detlaf, Ye. I., SOV/48-23-5-22/31
Selisskiy, Ya. P.
TITLE: X-ray Investigation of Interrelation in Processes of Recovery,
of Recrystallization and of Ordering in the Alloys Fe-Co and
Ni-Fe (Rentgenograficheskoye issledovaniye vzaimosvyazi pro-
tsessoy vozvrata, rekri stall izataii i uporyadocheniya v splavakh
Fe-Co i Ni-Pe)
'?ERIODICAL: Izvestiya Akademii nauk SSSR, Seriya fizicheskaya, 1959, Vol 23,
Nr 5, pp 640 - 642 (USSR)
ABSTRACT: The increase of free energy in low-temperature deformation by
tensions of the 2nd kind and the increase of the surface ten-
sion occur in consequence of texture destruction. For a number
of solid solutions, the increase of free energy is related to
the stoichiometric energy. These relations are shown in a dia-
gram (Fig 1), in which the solid solution consists of the com-
ponents A and B. In the case of low-temperature deformation, an
increase by the quantity 6 E m occurs in the free energy of the
solid solution which differs considerably from the stoichic-
Card 1/3 metric comnosition AB. The free energy of the stoichiometric

X-ray Investigation of Interrelation in Processes of SOV/48-23-5-22/31
Recovery, of Recrystallization and of Ordering in the
Alloys Fe-Co and Ni-Fe
composition changes by 11 En, and the total change of free ener-
gy is-equal to the sum of both these quantities. Thermodynamic
considerations are then made of the recovery, recrystallization
and ordering. Next, the results of the radiographic investiga-
tion of the'recovery and recrystallization of the alloys in
question are dealt with. The relationship between recovery and
the tensions of the 2nd kind and the distortions of the 3rd
kind, revealed by an amplification of the radiographic lines,
is made use of. A diaGram. (Fig 2) shows the ~iicrophotometric-
ally plotted curves of t~e K a doublet for three Fe-Co alloys,
annealed for 30 minutes at 400 0C. From the shape of these lines
conclusions are drawn as to the stage of recovery. Figures 3
and 4 show series of roentgenograms of the alloys Fe-Co and
Ni-Fe, annealed at various temperatures and different composi-
tions. Conclusions as to the stage of recrystallization are
drawn on the strength of the interference spots observable here.
Card 2/3

X-ray Investigation of Interrelation in Processes of BOV/48-23-5-22/31
Recovery, of Recrystallization and of Ordering in the
k1loys Fe-Co and Ni-Fe
There are 5 figures and 5 references, 2 of which are Soviet.
ASSOCIATION: Institut metallurgii im.
(Institute of Metallurgy
USSR)
L. A.. Baykoym Akademii nauk 888R
imeni A.k. Baykov, Lcademy of Sciences,
Card 3/3

S/137/61/tOO/'010/1D3OP56
A006/A 10 1
AUTHORS: Detlaf, Ye.I., Selieskiy, Ya.P.
,T.ITLE1 On the correlation of ordering, reoovery and reorystallization pro-
cesses in Fe-co alloys
PERIODICALs Referativnyy zhurnal. Metallurglya, no. 10, 1961, 42, abstract
lo:r,h264 ("8b. tr. Tsentr. n.-i. In-t chernoy metallurgii", 1960,
no. 23, 224 - 227)
ISM An investigation was made-with Fe-Co alloys containing up to 20-75%
Co. The alloys were subjected to cold rolling with 83.5% total deformation by
the 0.5 inm thickness and subsequent annealing at 150 and 7.500C In a vacuum bLt
different duration of heating. Subsequently the specimens were electropolished,
'IV was measured, and X-;ray examination was carried out by the method of reverse
exposure on Ko( ~.Co radiation. The lowest temperatures of recovery were observ-
ed in alloys of stoichiometrio composition. If a decrease of free energy, oon-
neated with recrystallization, exceeds the increase of free energy connected with
saft-ening, then recryatallization has a greattrr thermodynamical advantage and the
Card k/2

S11 7/46 1/000/10 10A30/1056
On zhe correlation of ordering, ... A006/AIOI
reorystallization process may cause softening. In the opposite case, softening
advances rearystallizition, In alloys with 35, 42 and 50% Cc both cases ooourl
this is manifested in the partial splitting-up of the double'..
P. Zubarev
[Abstracter's notet Complete translation]
Card 2/2

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