SCIENTIFIC ABSTRACT SACHKOV, V.I. - SACHOVA, E.

• Document Type: CREST
• Collection: Scientific Abstracts
• Document Number (FOIA) /ESDN (CREST): CIA-RDP86-00513R001446620012-5
• Release Decision: RIF
• Original Classification: S
• Document Page Count: 100
• Document Creation Date: November 2, 2016
• Document Release Date: August 23, 2000
• Sequence Number: 12
• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTRACT

KUM, M.I., prof.; SHROD, D.S., dotsent; SAGHKOV, V.I., land. med. nauk

ZHDANOV. Viktor Mikhaylovich; SOLOVITEV, Vladimir Dmitriyevich; -EFSHTL7N,

-~.,SACHKOV V,I,- qRIOORIYEVA,, M.P.; SPERA11SUY, A.I.; TROFIMOVA, T. M.
Bentonite test for diagnosis of infectious nonspecific ~olyarthritis.I
Lab.delo 7 no.7:9-12 Jl 161. (KRA :41:6)
1. Laboratoriya mikroimmunologii (zav. V.I.Sachkov) Gosudarstvennogo
nauchno-issledov,ateltskogo-instituta revmatizma Ministerstva
zdravookhraneniya,RSFSR.41
(BENTONITE) (ARTHRITIS)

FA C 67 -N* R SOURCE CODE, uW2- 58976 5/-OW/077/0072/0675-
7
AUTHORS: Zemakov, Ye. M.; Sadbkovp V.- Is'
ORG; none
TITLE: An experiment on the use of cesium frequency as a time standard
SOM-CE: USSR. Komitet standartov, mer i izmeritellnykh priborov, Trudy institutov.:
Komiteta, no.:77(137), 1965. Iasledovani~a'v oblaeti izmereniya vremeni i chastoty,~,
(Research in the field of time and frequency measurement), 12-75
TOPIC TAGS: cesium, quartz clockp frequency divider
ABSTRAdT: The performance of a cesium atom beam resonator was studied. The resonator
was constructed after the method of N. Ramsey,(Molekulyarnyye puchkit IL, M., 1960)t
and a schematic of the installation is presented. The performance ofthe, resonator
was com ared with two molecular,gen~rators (working on lines I - 3 and K - 3 respec-
tively) d with the eignals of the British National PhysicalLaboratory radia.station
F.
~GBR (on 3.g. 1). It was founA'that the constructed cesium resonator could be used to
determine the frequency of a standard quartz generator with an accoracy of 2 x 10-10.
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OY333
S/129/60/000/05/007/023
AUTHORS: Potak, Ya. M., Candidate.of Technical Sciences and
Sachkoy, V -and Popova, L. _Engineers
theL Intermediate
TITLE: High Strength StainlesSLL Steels Lof
Austenitic-blartensitic,Type Ji
PERIODICAL: Metallovedeniye iLtermicheskaya obrabotka metallov,
196b, Nr 5, PPL24-30 (USSR);
ABSTRACT; New types of stainless steels, characterized Lby an
intermediate austenitic-martensitic structurehave been..
developed recently in the USA (stee ls 17-7RN, AM350
AM355, 17-7Mo ) and Gt BritainL(steel~FV_520).L
steels have beendeveloped in the USSR anclthe p
of two steels of this L type. (SNAnd $N3)4are dp
in the present.article. The 6hemical composition of.,
the se stee 1S'L ip givenL in Table 1. . The L re lative position
of these steels in,the system of austenitic and
martensitic. steels is illustrated schematicallyL- in
2, kg/mm is plotted
where the 0.2% proof stress L(60
against the alloying elements c6ntent (increasing C,
N1 Ni , Or, Mo, and decreasingAl); the three curves
relate to,material subjected to the following:heat
Card 1/12 treatments: 1 - quenching; 2,- quenching and L.
cmh-,7.P-rn t
rpatmentt 3 auenching:- sub-zero

69333
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E193/E283
'High Strength Stainless Steels of the Intermediate Austenitic-
Martensitic Type
treatment, and tempering; the~figures given by.the
curves indicate the.approximate values of.50..~; the-
intermediate.steels arein the shaded region, the
martensitic and au'stenitic regions being to.,the left
and right respectively. The intermediate steels have
certain specific properties., Inthe water- ~or'air-
quenched condition they have, mainly austenitic structure
characterized by low hardness and yield point..on:one~~
side, and.high ductility and toughness on the other.-
In comDarison with the austenitic steels steels'of
the iniermediate type have relatively high UTS,.,owing:
to the fact -that, as a resultof plastic deformation,
martensitic transformati,on.,takes.pl~.i6e,in thetensile:
test pieces. Intensive formation.of martensite takes
place during the sub-zero~:treatment.. This leads to-
an increase in UTS,,dnd.particularly in the..yield point;
since, however, a considerable, proportion of austenite
~Card 2/12 is retained after this treatment, the obtained material

69333
000/05/007/023
S/129/60/
E193/E283
High Strength Stainless. Steels of the Intermediate Austeni-tic-
Martensitic Type
is both strong and ductile. The martensitic.transforma ~tiIo n.
t c n
akes pla e also~during.plasticdeformatio (rolling,
drawing, forming, etc) of.the intermediate steels;.. the-
intensity of the transformation depends on~thetempera-..
ture; at,temperatures higher than N the mart 6n'sitic
transformation does not occur. Withdincreasing content
of alloying elements that lower the,temperature,of the
martensitic transformation (C, NI Nil~Crl Mo, Mn) the
character of steel changes from martensitic to austenitic.,
This is illustrated by data reproduced Fig 2 where
the mechanical, properties 6b .(UTS. kg/mm-).and.6 0
(0.2016 proof stressi kg/mm2) of steel SN2, are pl-,ded,
in '6kel content C e 0 other alloying
aga' st the ni (the ont nt f,
additions isgiven in the caption); t -he curves were.
constructed for specimens siibjected.to the following
heat treatments: 1,- auenchingfrom 10500C; ..2.- quenching
from 10500C 1, 2 h treatment at. -700C; 3-- as in (2) and
then tempere&at.15000C for,.l,.h; 4 0 -quenching *.from,
,Card, 3/12 7600C and tempering f or 1 h at 500 C. It.will be.seen

69333
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E193/E283
High Strength Stainless Steels of the Intermediate Austenitic-
Mart6nsitic Type
that steels, containing,6.68 to 7.4%~Ni, are martensitic,.,
of course,
those with 8 76 to 9,57% Ni are austenitic
the proportion of nickel, necessary t6impart to Ia
steel the intermediate properties, may change for a
material with a different content of other,alloying
additions. Theeffect of titanium and aluminium content,.
~on the mechanica) properties of steels containing 0.0,1% 0,
0.3% Sil 0.7% bin, 16.0% Cr, and 6.8% Ni'in the'former-
case and O.OG% 0 0.250/6 Si 0.82% Un, 16.196 Cr, and
6.6y, Ni, in the latter case, is illustrated in Fig 3
wherel~.2 and rDb aretplotted against the Ti (graph' a).,,,,..
and A graph b) con-ten curves 1 and 2 relate
to steels 1 - quenched from 10500C and 2 -.quenched,from
10500C and tempered at 5ob0c for 1 h. It will.be seen
that increasing the content of aluminium,' which raises,
the martensitic.,point of steels, results in changing
the.steel structure to,martensitic, and.accelerates
Card 4/12 the temperin- tension. Introduction of,titanium,,Which

69333
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E193/E283
High Strength Stainless-Steels of the Intermediate Austenitic-
Martensitic Type
forms carbides that are not-easily soluble~ decreases,
the carbon content in austenite and so raises the
martensitic point; the rate oftempering is..also
accelerated by addition of titanium.~ Steels With,certain"...
alloying elements may contain delta-ferrite,,in which'...
case the limits of the alloying elements content within.~-
which a steel will retain its intermediate character-
become wider. This is,illustrated by,comparing curves
in Fig 2 (for steel SN2, not containing:delta-ferrite)
with those given in Fig.4 (for'steel-SN3 which contains
20 to 2-'Plo delta-ferrite)~ where 6 and 6 a
b 0 2, re plotted
against the Ni.(graph a) and Mo (graph b) dontent-1, the..
content of other alloying'elements being givenAn.,the
caption; curves,l and 2: relate to,.Material' 1. - quenched
from 10500C and:2 - quenched from:10500C, treated at~.
-700C for 2 h, and tempered at 4500C. It,has ~een~found
that, in the presence of delta-ferr,ite, the,content,of
not only nickel, but.also molybdenum.and carbon in-,
the steel can beconsiderably varied without affecting.:
Card 5/12

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High Strength Stainless Steels of the Intermediate Austenitic-.
r-Aartensitic Type
its intermediate character; no plausible explanation
of this effect has yet been found The position of,the
martensitic point of steels of.th~ intermediate type,
can be appreciablychanged by varying the auenching
temperature, as a result of which the position of
austenite changes owingto dissolution or precipitation.
of carbides. This.is illustrated by data, reproduced..
in Fig 5, where 6b and 6 02 of an experimental steel I
containing 0.11%. C1 15-09 Cri 8.2/116,Ni9 0.6%2, Tis
0.26Yo Al (graph a) and.steel-SN3, containing 0.09% C7
16.90/6 Cr9 4.8%, Ni, 3.25% Mo, 0.51% Mn(graph b) are
plotted against.the quenching,temperature (OC); the,
various curves relate to material l.- hed
as,quenc
and 2 - quenched, treated at,7700C.for 2 h and.tempered
7
at,5000C (graph a),or 4500C (graph..b). It will ~ -be seen
that although the intermediate steel SN3, containing,
17% Cr and 3. 5016 Mo. has a very high strength: after
.Card 6/12~air-quenching from,Ii9500C~ followed by sub.-zero ~tr.eatment

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E193/E283
High Strength Stainless Steels of the Intermediate Austenitic-
Martensitic Type
some melts of this steel did not harden when quenched
from tem-Deratures:higher than,10500C. This is explained
by the fact that after the chromium and molybdenum
carbides have been dissolved, austenite becomes so
stable that no martensitic transformation occurs during
the sub-zero-treatment. Titanium-bearing steels may-
change from martensitic to intermediate type if the
quenching temperature is raised to 10500C (Fig 5), so
as to dissolve titanium-bearing carbides; further
increase in the quenching temperature leads to the
formation of almost fully aus.tenitic structure and brings
about a decrease in the yield point and a slight increase
in the.UTS, Strength of steels of the intermediate t ype
increase considerably during plastic deformationl the..
increase in the yield point being more rapid.than that
in the UTS. This is illustrated by -data, reproduced in,
Fig 6, where 66.2 and 6b. Ckg/min2, left-hand scale)
proportion of.martensite (x, and elongation .61 %1
Card 7/1-2 right-hand s,cale.), are plotted against.thedegree Of

69333
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E193/8,283
High Strength Stainless Steels of the Intermediate Austenitic-
Martensitic Type
plastic deformation by cold rolling;. the curves., CO.n-
structed for steel,SW2, relate to material.1 --~. a If t er
deformation, and 2 - after deformation followed by
-tempering for l.h at 48000. Itis pointed out, in.
this connection that1whereas tempering of cold-worked
steel increases its UTS only in the case of a high,degree__
of deformationj the yield point increase.s even.in lightly,,
deformedmaterial. Not only strength, but also elonga-
tion of cold-worked, intermediate steels, is increased
by tempering; a decrease in ductility after tempering.
is observed only in heavily deformed steels of this type.,,
The optimum results are obtained by tempering at 450to -1
500OC; this is-shown in Fig 7, where CL (90,) M6 0.2
6b,' and 6 of. steel SN2 are plotted against:.the.
tempering temperature formalterial tempered1for 1 h
af ter cold def ormati-on,.(graph a) and, af t'er 4uenchlng
followed by a 2.h.treatment at -700C~(Sraph b), The
card 8/12 sub-zero 'U'reatment as a.,method of increasing strength of-

69333
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E193/E2831
High Strength Stainless Steels of the Intermediate Austenitic-
Martensitic Ty
p e
steels, was first-suggested in USSR by Gulyayev (Ref 6);1-1
beside cold-working, this treatment is one of the basic
methods of hardening steels of the intermediate type.. 11
The effectiveness of this treatment depends largely on
whether the given steel is more austenitic orlmartensitic.,.
in character, and on the extent to which carbides.are. .1
dissolved in austenite. This is illustrated by data'.
reproduced in Fig 81 where-the left-hand graph shows the.~
variation.of 00 2 as a function of the temperatureof
the sub-zero tr6atment of 2 h,duration, the.right-hand
graph showing the variation of .6 2 as afunction oV
time (10, 30-min, 19:2 h) at '-7008,- curves I to, 4 relat,e'
to steel containin ~% Ni
Ig 8.76%, 7.35%9 7.75% and 7.1. 1
.respectively., The sub-zero.treatment yields optimum
results when carried out at --,700C its effectiveness
decreasing at lower.temperatures. The,martensitic,
6,ransformation.during'.the sub zero treatment takes
place isothermally; -the rate of transformation during:.
0 e own by pre liminary
Card 9/12 th6 f irst I t 2 h. can be slow d d

69333
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E193/E283
High Strength,Stainless Steels of the Intermediate Austenitic-
Martensitic Type
stabilizing treatment which can be carried out.by one of
four different methods: (1) heating to 150 to 5500C;
(2) cold deformation of 1 to 100/6. (the lower the degree
of deformation the better); (3) slow cooling to the
temperature of the sub-zero treatment; (4) cooling
the steel to -3000 before subjecting it to the sub-zero,
treatment proper. Steels SN2 and SN3 can belfabricated
in the form of soft, half-hard9 and,41ard stri]~and sheet
as well as in the form,.of rods, forgi ngs, wires and:
extruded sections. Steel SN2 should not be hot-worked
above 12000C;, owing -to thepossibility of. the presence,
of some delta-ferrite in steel SN its maximum hot-..
working.temperature is about 1050 0; the lower lim#~.
of the hot working range fo .r both st.eels is.8000C.,
Typical mechanical properties'of steels SN.2 and,SN3
are given in.'Table 2 -tinder the followin&headin s:
type of the product prods; plates (strip); rod; plate
trip)-. dittol cohdition and heattreatment
C ard 10/12-s

69333
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E193/E283
High Strength Stainless Steels of the Intermediate Austenitic--
Martensitic Type
(quenching froin 10500C, ditt-0 quenching from 9750C
SIT2, or .9300C, SN3 followed by 2 h,treatment at -70?C
and tempering at 4~50C, SN2 or 4500C.SN3; -ditto, but
steel SN2 quenched from 9506C; cold-rolled, half-hard;
ditto.followed by tepering); 6 6 6 impact
strength aki k9m/cm , of steel PN2 anH*3. 'Owing to,
its high Cr (17016) and Mo (3%) contents, and the,presence,
of delta-ferrite, steel SN-5 is more corrosion-resistant~,
than steel SN2. Both steels can be easily Welded,.steel;
SN3 being used in'both cases as the welding rod; 'no
heat treatment after welding is necessary. The article
is concluded by a list of several recommended,heat treat-,
ment procedures for steels.SN2 and SN3. (1) To improve
machineability: heating to 7500C. cooling to~20OC9 and...
re-heating to 650OC; the structure.produced by this
treatment consists of martensite with some residual
austenite and carbidesi precipitated at~the grain boun-.-...~
daries, (2) Quenching, preliminary to the- sub-zero,:-,
treatmentt rods and forgings,of steel SN2.are quenched
Card 11/12

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AACC
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NK1 AP60029iO
65/000/024/0073/0073
UR/0296
SOURCE
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INVENTOR, Sachkov, V. V ;:Pot k Y
a a. M. Lavrov V. 1. Popova i L. S.:;, Grashchenkov,~,
P. M. --------------
ORG: none
A
TInE: Stainless steed. Class No. 177081

SOURCE: Byulleten', izobreteniy,i,.t ~nykh'znak
ova ov,,ln6,. 24 9 J9659,.~ 73 A
TOPIC TAGS: steel, stainless 's tee I chromium'- containing steel. ',nickel.: containing::,,,..
steel, manganese containing steel.:.
ABSTRACT: This Author Certificate:introduces a stainless steel'with'improved mechan
~ical . properties that contains.0.05 0. 09% carbon,,, lZ'max manganese,,~, 0._7%. max, silicon,
15.5-17.5% chromium, And 5.0-9.0%'~nlckel
[AZ]
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SUB CODE: Il/ SUBM DATE:: Oliun63/ ATD: PRESS: .
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SOV/120-58-5-13/32
A.A., Dmi,triyev, A.B., Kosmarskiy, L N. Sachkov
Yu.N Sbitnev Ye.A. Kheyfets, A.B. Tsi-G'Lias'hvtii:~S.~-
L. S.
TITILE A Vacuum. S-oark Switch (VaL-uumnyj-e iskro-~-rje reie)
P'~;QIODIJAL: Pribory i tekhnika eksperimenta, 19581 Nr 5, pp 53- 58,
(USSR)
ABSTRACT: The device consists of an evacuated glass..envelope,which
contains 3 clectrodes (see the' general diagraim.of Fi6- 1)
The principal discharge gap comprises a complex cathodes
consisting of tylo electrodes which form an auxiliary, dis-
charge gap. T-Ibe two cathode electrodes are separated by
means of a fine mica plate; when a triggering pulse is
applied a discharge is formed on the surface,of the mica.
Fig.2 shows 6 alternative solutions of:the electrode systems
of vacuum s-oark switches.- Fi 3 shows photographs of actual
swituches (tubes 4, 5, 6 an _51and photographs of. 3 thyra-
rons Of'OCOM,
(tubes 1, 2 and 3).for the purpose parison. The
basic parameter of a.switch is its anode.voltuage V its
oDerating current I and its triggering breakdown voltage
The anode operating voltages up to 20 k-V could be-~~
V-11
obtained with a discharge --ap of.1 mm. The values of the
Card 1/3

_30V/120-58-5-13/32
A Vacuum S-,)ark Switch
oar-,e current are determined primary
sc-' 1y by the exteT- al
para-, 'he switch is employed.'
meters of the circuit in whicht
The. currents can be very high since the -tube is "extinguished"
at a current of about 20,A. The energy required for the
initiation of the main-gap breakdoun is very small. Thus.
the switch can be triggered by the energy stored in a
caDacitance of about 5 at., but the triggering voltage should
be at least 1500 V. The switch is subject to some time
delays. T-',-,e overall delay is, T=tl + t2 + _G where
t is the time between the commencement of the trigggerin,-
1
PLLlse and the incention of the trig;-~er gap discharge; t
C)
2
i
-he time la.:~- between the commencement of the auxiliary:
s U
dischar-e and the inceDtion of the main-gap discharge, and!
0 0 - C3
t- is the formative time of the main gap discharge..~These
C)
ted - ap
Lme delays are illustra gr hically in Fig -4 In actual
c3
UL-Coes t1ae formative times of the main di -scharge were of.the,
ord~:,-r of 0.03 -jLs. The el,~ctrical characteristics of a s-oark
2/3

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SOURCE CODE: UR/2667/66/000/037/0118/0129~
Acc mR. AT6034376
UTHOR: Sachkova, A. 1. (Deceased)
~ORG: none
~,TITLE: Characteristics of air pressure distribution over seas
SOURCE: '11-loscow. Nauchno-issledovatel"skiy institut aeroklimatologii. Trudy, no. 317,.
1196.6. Voprosy.klimatologii (Problems in climatology), 118-129
TOPIC TAGS: atmospheric circulation, atmospheric pressure, oceanography
ABSTRACT, This paper gives charts of air pressure distribution o *ver the Caspian,
Barents, and Japan Seas. Data from hydrometeorological observations by,vessels.at sea
were used'to construct these charts. The charts are analyzed and the main conclusions
are: (1) these pressure charts are qualitatively new and make it possibleto make a
!nearer approach to study of the pressure distribution field ibove sea.surfaces;1(2)
:the thermal state of the sea surface exerts a-far greater effect Ion the pressure.field
;distribution over seas, particularly in the summer months (when.the centers of atmos-,
pheric action become weaker), than was.believed.before utilizing the results of ship-..
.board observations in compiling these charts; (3) Octoberis the transitional month
in the restructuring of the pressure field to the winter conditionsAn all the seas
studied; (4) the transition to the summer conditions occurs from April to,June, depend--
in- on the latitude of the sea; this is April for the Caspian, May for the Japan, andl
June for the Barents Sea. Orig. art. has: 5 figures.
Lj~~:d 1/2
'Z/2
I Cor

Role of the p3ych-)gezil--- I-Ji-tO th, d~jv~r-' 1; y!
11h~--,--a.,,3m. T-miy Gcs. psl~hP
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P9= 7B(XK E%rz-.TATICN 507/4617
".-I~miyl n.uk =R. I-L-17% pc kh12ii
41. 'Ap, Is's '""s 3
m
(J~rtesv I-@ t -%d7. --cm. 10) Zrrsta ollp Inserted, A, %4 acpLea printed.
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1-1 T.L. -go.X.&1#s1jN ;~, b.1itich-koy WALL
4osp. FA.'t A.?. Tlzcg~dcv, 1-46ILcling U. or Publishing Hoqsa, A.'~ ButkiltW1
Ttch. Ed. i V.I. Bmx4ull.
t*.?.F= t 'his book is tml..dd f., Ieb~m-..r p.rs.u.1 a.-.-,d Ith g.8
D.1y.Is In ".-la.
CCV17=1, This C.11"tion or or% Islas Is bisd on of on
Aslytic.l chalas r7 AS USSR on 3r.tle Ic ~It~. OA nelysts -t,1s.
L
Th. rtItIro ;r."n. ~Iat. The IKC-~f~ioft -thVI. d~v,l:p~A by Z~-
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of p..o in other 2) no Z.M., t
time or
mh~%Ivtry wW A~Iy`.Atal Ch-istry !=nI V 1. 7*~~dskijr
AS U-54111, Mc.cow, mki.g It ;~oswibl. to _c4zat* the practlastrility ~.d fliLls
of ppllt.tloa of t" d-11f.-t w II- Ice' ;methds., 3) -.he etntrItU-41~
To. A. Eyschko and c~--k-rs In Mir study ~f themodyrnmic mnth~ds for u-
1-tio. of r~it.bl, cmdIttoos f-r s:1.IY,i.1. 4) Tlo d,t.r
alt.tion or gas.. 12 u.ts.,s by the mulfw~- ne-thod - d ... I~pl by A.K. 3.b-
1h. o;ect.-= -tl,,,l for t2l. of hylr~g-
davvl~p~d by A.S. Zardell' L=4 s~ttors cV th~ao ~.t lc*,,4 oyj-
11-111" end re"- Tqtt..1!T the %pious -41rlo.l 1.vorl be th~
".4 In sualrala. and L-dIcato the bsol-c t-nda ~f rovoamh. aef-,
khall~h-kay71...- Iw% 1-o1
1-I'd P.7., end R.,A;,M, (umllskiy pil-lt
1-3 S-4. Er.
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et 6f &U1
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3,qrdj~sk]. Sffwl of I-". the Hpiroge.
3%441 -37
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d!.th
49
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4-1 r4s.4 in
t.- t.,. C-.kh!:s! I Ikh-IL 11.~Ai
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V.1 ve~.dsuT AS
C..s Is by *be I-p& of the Feri*dit Sy.t- et EI.:f
82
itute ~' re,~hmimtr7 4nd ki-jl-
Mosn .. ..
xjg4ft in A.1kall t1waLs -d is Ljj~ys -1 the Me.~,x7
91
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G-h-d.t~y ~d A-
Ch~tstry iwc~t V.I. TomAIN)"Y A3 75jR, Z'~teminsti~m cr
",I in 'a -.hzd 103
%~o Alk--j.. E.r-:h 'I th. Distill -.1- Me
"d
C.och-tit:7 and Aam-Irtizal Chamistry Immn.- V.I . m,4jk-
A3 U=, 7he Method Wit-6, the -.A- -f I Pl-ttolss -t
f~r the D.t.-RI.AtIcll ~f in Y-t*1A log
Mthoda of ?-";*rig Ans1r.1-m-1 of Alksu !I,*-:-
Nz~ f:r V3outna Extrao-.1--a 117
11,2-1, Lj_1 -1.1 d Z.m. %r~tj.'4 [institut of Gt
iv..J. V.I. -rmmdak17 AS USSR, X~s
.n~
72m of I-Rv Difrsc-Im F~,aes Amnlysis *:r -he Determination or C%Iod in
et Is ~?22
m
e

SAMOVA, Z. I.
USSR/Chemistry Chemical Engineering, Distillation
.Card 1/1
:Authors Sacbkoval, Z~ Y., Trushchev, G. A
Title Corrosion under the.conditions encountered in the synthesis W
methanol
Periodical Khim. prom. 4, 50-51 (-C42-243), June 1954
AbEtrac. State that intensive corrosion takes place in pipes through which com-~-
pressed gas for the synthesis of methanol- is ~conducted between*,factory.
shops, and that this corrosion is due chiefly to the action of-hydrogen
sillfide and of other siz1fur compounds. On the basis of the data. cited,:
come to.the conclusion that pipes made of steel of the,grades.30HMA
and 1`,,KhMA last longest under the conditions of methanol production:and
are to pipes of carbon steel Grade 20 or pipes provided. with
a stainless steel lining. Five figures, one table.
institution Berezniki Nitrogen Fertilizer Plant imeni Voroshiloy

BOGOSLOVSKIY, Andrey Mikhaylovich; ZIWIOVICH, Vasiliy Leontlyevich;
MATVEYEV, Yevgeniy Nikolayevich; MUMZI, Georgiy Fedorovich;
RSHANNTSKIY, Boris Antonovich; IMESNOV, Viktor Ivanovich;
NOVIKOV, Georgiy Nikolayevich [deceased]; NUDIGA, Pavel
Korneyevich; SAPRYKIN, Aleksey Petrovich; q~PUQVSKIY
Georgiy Semenovich: FRENK, M.TS., obshchiy red.--M?=AV,
S-
-"'TMMQVA, Ye.A., tekhn.red.
[Textbook for engineers' onlia"rine internal combustion engines]
Uchebnoe posobie dlia mekhanil~a III razriada po,sudovym,dviga-
teliam vnutrenne.-o agoraniia. Izd.2., perer. Pod obshchei red.
M.TS.Frenka. Moskva, Izd-vo 'Morskoi transport," 1959. 711 P.
(Marine engineerinK) (MIRA 12:9)

(Boats and boating)

'Conitteg. on Si,~.~ i,, lp tf Qr
It, an d tplreri+ Wn a Uuat t4e fo U. -ma, fig. P-clentl-OLIC vorkfi, pop-,,l ar, en -
booka, and t-rxtbwk* have 6een,t-tjbw.1ttpd for compe-tition for ita.11n, FrIzes, for
'Ole M 1954'
T t U- rf
Sokolo,.r, 11. S. "Elements of Farm. inr" Moscow Agricultural Academy
Yarkov, 5). P. (te-xtbook) iTaeni K. A. miryazeV
iy ,1'l
Chizhevsk
Cherkaso,r A. A.
Shestakov, A. G.
Gulyakin, I. V.
Peterburffsk-iy, A. V.
Troitskiy, A. It.
Li:&Iyanyuk, V. !
Savzdarg, E. E.,
Trofimovich, A. Ya.
Kuznetsov V. S.
Kudryavtsev, IT. Ye.
Pronin A. F.
Alekhin TIT. V.
'Sachli,