Effect of Thermo‐Plastic Treatment on Structure and Corrosion Properties of High Nitrogen...

8/22/2019 Effect of ThermoPlastic Treatment on Structure and Corrosion Properties of High Nitrogen CrSteels

1/10

JournalofMetallurgicalEngineering(ME)Volume2Issue1,January2013 www.mejournal.org

19

EffectofThermoPlasticTreatmenton

StructureandCorrosionPropertiesofHigh

NitrogenCrSteelsVeraV.Berezovskaya

Instituteofmaterialscienceandmetallurgy,UralFederalUniversitynamedafterthefirstPresidentofRussiaB.N.

Yeltsin/Professor

ul.Mira,19,Yekaterinburg,620002,Russia

[email protected]

AbstractEffectofagingonstructureandcorrosionpropertiesinhighstrength austenitic Crsteels alloying with nitrogen Cr21N1

andCr18Ni2N1hasbeeninvestigated.Structureofthesteels

and kinetics of austenite decomposition during the

treatment was studiedby Xray diffraction, TEManalyses

and electric resistance measurements. The highest valuesof

strength, micro hardness, corrosion rate and relative

strength reduction as far as brittle intergranular fracture

wereobservedattheearlystageofaustenitedecomposition

at the aging. The formation of nitrides CrN as well

martensitestressinducedtookplaceinthesteels.According

to resistormeter investigationsofnitrogen steelsincompare

withcarbonsteelCr18C1attheearlystageofaging(350C)the metastable ordered clusters enriched with chromium

and nitrogen were formed. Growths of aging temperature

up to 500C led to dissolve the carbides or nitridesbut at

600 C discontinuous precipitations were observed nearby

thegrainboundaries.

Effectofagingcombinedwithcoldplasticdeformation(CPD)

at an 824 % reductionby two schemes,before and after

aging at 350C, on structure and related corrosion

propertiesofsteelCr18Ni2N1hasbeenstudied.CPDatan8

12 % reductionbefore aging at 350C was shown to thrice

decreasing of corrosion rate of the steel as compared to the

undeformed state.A thermoplastic treatmentby thesecondscheme with using CPD at an 20% reduction after aging at

350 C is found to be more effective: the corrosion rate

decreased by an order and strength reduction decreased

morethanbyfourfoldascomparedtotheundeformedstate.

KeywordsAustenite Decomposition; Ordered Clusters; StressMartensite;

Lattice Parameter; Stress Corrosion Cracking; Cold Plastic

Deformation.

Introduction

Highnitrogensteels(HNS)duetotheirmorestrength

and corrosion resistant than in other austenitic steels

with carbon are widely used in power machine

building,shipbuildingandotherfieldsofengineering.In the nearest future [19] after perfecting their

manufacturing technology they are expected willbe

applied in abigger industrial scale. One of the main

directions of investigations to solve these problems is

searching a way to increase their resistance to stress

corrosioncracking(SCC)bothbyefficientalloyingand

optimizationofstrengtheningprocedure.

Well known that nitrogen includes a significant

contribution in hardening of solid solution and grain

boundaries as well as in strain and precipitation

hardening. According to data from work [2],

realization of these factors at appropriate degree of

coldplasticdeformation(CPD)canprovideextremely

high strength for this class of steels up to 3600 MPa.

However in a certain structural state they are

subjected to SCC in corrosive environment [10, 11] so

in this case expedient to use them after strengthening

notmorethenupto0.2=1400MPa.

Materials and Procedure

The highstrength lowcarbon steels with highnitrogen content (0.91.0%) Cr21N1 and Cr18Ni2N1

have been investigated to study mechanism and

kinetics of austenite decomposition and clearing up

CPD influence on structure and corrosion properties

of steels. Kinetics of decomposition of the

oversaturatedsolidsolutioninHNSwascarriedout

as compared with high carbon steel Cr18C1. Their

chemicalcompositionispresentedinTable1,firsttwo

of them were producedby nitrogen pressure casting,

homogenization at 1250 C and rolling with further

quenching in water afterbeing exposed for one and

half an hour at 1200 C. The high carbon steel was


2/10

www.mejournal.org JournalofMetallurgicalEngineering(ME)Volume2Issue1,January2013

20

manufacturedby standard technology and quenched

from the same temperature in oil to put the austenite

structure. The specimens prepared for testing were

agedat300500Cfortwohoursandat600Cforan

hour.

TABLEICHEMICALCOMPOSITIONOFSTEELS

The general corrosion and SCC tests were performed

ina3.5%NaClaqueoussolutionasitdescribedinthe

work [10]. Fractographic studies of fracture surface

after SCC were examined on a JSM35C scanning

electronmicroscopeandmetallographicexamination

onaNeophot32opticalmicroscope.

Theelectricresistancemeasurementswerecarriedout

to investigate the kinetics of solid solution

decomposition [12]. Xray diffraction analysis was

carried out on a DRON3 diffractometer with cobalt

radiation and a radiation filter. The austenite andmartensitecontentsinthesteelswereestimatedusing

the method of homologous pairs by comparing the

integratedintensitiesofthe(110)and(111)lines[13].

The structure of austenite and the type, morphology,

and size of additional phases were investigated by

transmission electron microscopy on an EMV100L

electronmicroscope.

Results and Discussion

Mechanical properties of high nitrogen steels werefollowing: yield strength (0.2) is 650 and 610 MPa;

specific elongation () is 21 and 18% after quenching

and0.2=780 and 820 MPa; =5 and 9% in aged state

respectively in Cr21N1 and Cr18Ni2N1 steels. The

highest growth of strength, corrosion rate and

susceptibilitytoSCCin3.5%NaClwasobservedafter

aging at 350 C [14]. The fracture of specimens was

brittle and intergranular in this case (Fig. 1, a) while

the destruction was not associated with nitrides,

located along the grainboundaries. After overaging

the resistance to SCC increased and the intergranularfracture was replaced to quasicleavage including

related to colonies of discontinuous decomposition of

solid solution (Fig. 1,b). Theinvestigatedsteels had

a good passivity in all structural states due to high

contentofchromiuminsolidsolution,howeveratthe

stage of active corrosion the sharp acceleration of

corrosion was observed after aging at 350 C ininvestigatedsteels(Table2,line2).

FIG.1FRACTURESURFACEAFTERSCCOFCR18NI2N1STEEL

SUBJECTEDOFAGINGAT350(a)AND600C(b)

After quenching from 1200 C an austenite and

carbideswithsurfacemartensite werenotedincarbon

steel as well as in nitrogen steels (Fig. 2, a,b). The

structure of high nitrogen steels varied with rising of

aging temperature identically with some more

stability of austenite in nickelfree steel. The

microstructure of nitrogen steels aged at 350 C was

almost similar to quenched one (Fig. 2, c),but after

agingat600Citwasratherdifferent(Fig.2,d).

Martensitesoftwomorphologieswithdifferentlattice

parameters aT=0.287 nm and a=0.291 nm was

discovered in steel Cr18Ni2N1. As it was shown

earlier [15] it was the thin dispersive martensite (T)

onthegrainboundariesandannealingtwins(Fig.2,b,

c) and lensformed stressinduced martensite () in

the middle of grain (Fig.2, d), which formed

respectively from austenite depleted and enriched

with chromium and nitrogen. The same picture was

found after SCC. The results of Xray diffractionanalysesareshowninTable2.

Steel

grade

Contentinthesteel,wt%

C N Mn Si P S Cr Ni

Cr21N1 0.020 1.021 0.19 0.42 0.015 0.010 21.45

Cr18Ni2N1 0.008 0.899 0.30 0.27 0.020 0.010 17.86 2.00

Cr18C1 0.920 0.63 0.79 0.025 0.023 18.30

30 m

15 m b


3/10


21

TABLEIIPHASECOMPOSITIONANDCORROSIONPROPERTIESOFTHECR18NI2N1STEELAFTERVARIOUSTREATMENT

of

treatmentSchemeoftreatment

Contentofphases,%*

m,

g/m2h st,%Intheinitialstate AtthesurfaceoffractureafterSCC

AgingwithoutCPD

1 Quenchingfrom1200 95 5 0 62 26 12 2,0 352 1200 +350,2h 95 5 0 58 22 20 30,0 37

3 1200 +400 95 5 0 62 22 16 8,0 34

4 1200 +600 50 44 6 28 64 8 1,0 29

5 1200 +700 0 100 0 0 100 0 0,5 21

CPD

before

aging

6 1200 +8%CPD+350,2h 89 5 6 10,0

7 1200 +12%CPD+350,2h 87 5 8 11,0

8 1200 +20%CPD+350,2h 50 15 35 40 15 45 55,0 42

9 1200 +24%CPD+350,2h 80 7 13 50,0

10 1200 +20%CPD 95 5 0 0,3

CPD

afteraging 11 1200 +350,2h+20%CPD 95 5 0 95 5 0 2,5 10

12 1200 +400 +20%CPD 95 5 0 0,3

13 1200 +600 +20%CPD 50 50 0 0,8

14 1200 +700 +20%CPD 0 100 0 0,4

*Withoutexcessphases.

FIG.2 ICROSTRUCTUREOFSTEELSCR18C1(),CR21N1(B)QUENCHEDANDCR18NI2N1(C,D)AGEDAT350AND600C

30 m

30 m d

c30 m

20 m b


4/10


22

According to comparison of SCC tests and Xray

diffractionresultsthecorrelationbetweenthevalueof

relative strength reduction (/K) and quantity of

stressinduced martensite, formed directly during the

tests, is observed in high nitrogen steels. Thebiggest

portionofmartensiteinstructureofsteelwasnotedafteragingat350C.

By transmission electron microscopy of thin foils the

evolution of structure in steel Cr18Ni2N1 under the

aging was studied. The structure of quenching steel

consisted of austenite (Fig. 3, ac), ratherbig particles

ofnitridesCr2Nretainedafterheatingalongthegrain

boundaries and not more than 5% of Tphase as a

result of martensitic transformation in depleted

austenite near the nitrides (Fig. 3, df). The nitride

Cr2Nhasahexagonalcrystallinestructurewithlattice

parametersa=0.4805nm,c=0.4480nm. Thecrystalsof

surface martensite formed at electrolytic polishing of

foilcouldbeseenaswell(Fig. 3,g).

After aging at 350 and 400Cbesides andphase

ultra dispersive nitrides CrN with FCC crystalline

ordered structure and lattice parameteraCrN=0.415 nm

formed from a supersaturated solid solution due to

homogeneous isomorphic decomposition were

observed (Fig.4,ac). The crystals of martensite

were found as well. Both phases CrN and were

noticednearbytheextinctioncontoursintheplacesoffoilbending(Fig. 4, df). After 2hour aging at 500C

besides Tphase in the settlement of discontinuous

decompositiononthegrainboundaries(Fig.5,ac)the

singlecrystalsofmartensitewerediscovered(Fig.5,

d). At temperature 600 C fresh portions of

discontinuousdecompositionsettlementsconsistingof

nitridesCr2NandTmartensitewasobserved(Fig.6).

The electric resistance of the steels Cr21N1,

Cr18Ni2N1 and Cr18C1 has been measured

depending on time of aging in isothermal conditions

at 300, 400 and 500 C (Fig. 7). These dependences

wereshowntobethesameforhighnitrogenandhigh

carbonsteels.Attheinitialstagesofprocess(36h)we

can see a sharp electric resistance decrease which

becomesbigger as the temperature of aging grows.

The effect of aging depends on a super saturation

degreebyinterstitialatomsofaustenitequenchedbut

at the same content of carbon and nitrogen (about

0.9%) its displayed stronger in high nitrogen steels.

Withtheincreasingofthetemperatureatthisstageof

aging a differencebetween the curves reduced and

they practically coincided at 500 C. The stress

recoveryattheheatingwasresponsiblefordecreaseof

electricresistanceofthesteels(sharpdecreaseofR/R

preagingstage).

At a longer time of heating it was an increase of

electric resistance most pronounced at 300C. This

stage continued not more than 7 hours at 300 C, 4

hoursat400Cand1hourat500Candassociatedwith the separation of the solid solution with

chromium (as well carbon in carbon steel) during

these exposuresbecause of the conductivity electrons

are scatteredby these enriched in chromium clusters

[16](sharpincreaseofR/Rstage1).

Longer aging influenced on the curves character

differently depending on the temperature of aging. It

is necessary notice a stabilizing of decomposition of

austenite in carbon steel at 300 and 400 C and in

nitrogensteels

only

at

300

C.

It

is

connected

with

the

formingofcarbidesincarbonsteel,butnotcompleting

of nitrides formation in nitrogen steels. It needs to

continue the heatingand further slow increasing of

electric resistance which observed at 400 C in these

steels confirmed it. This process associated with the

orderinginchromiumenrichedclusterswithnitrogen

that was able at an exposure at this temperature or

understresses(nearbytheextinctioncontoursFig.4,

a) if exposure was not enough. Thus the formation of

carbides or nitrides characterized with unchanging or

slowincreasing

of

R/R

stage

2.

Decreasing of electric resistance at 500 C hasbeen

shown in all investigated steels and was connected

with dissolving of clusters enriched in chromium

(slow decreasing of R/R accordingly in carbon and

nitrogensteelsstage3).

Effectofcoldplasticdeformationonthephasecontent

and corrosion properties of the steel Cr18Ni2N1 is

presented in Table 2. CPD at an 824% reduction was

combined with aging at 350 Cby two ways:before

(lines 610 in Table 2) and after aging (lines 1114) as

compared to the undeformed state (lines 15). It

follows from Tab. 2 that CPD at 812% reduction

before aging at 350C decreases to thrice a corrosion

rate in spite of some increasing of martensite

content. On the contrary CPD at 20% reduction

increases nearly twice the corrosion ratebecause of

considerable depleting of austenite and as

consequence increasing ofTmartensite content after

strain aging. Furthermore this treatment condition

negativelyinfluencedontheSCCofthisnitrogensteel

and increased ofmartensite content if to compare

withundeformedstate(lines2and8).Itisknown[17]

thatalowlevelofstresses(trthresholdstress)


5/10


23

FIG.3STRUCTUREOFQUENCHEDSTEEL CR18NI2N1:ASUBGRAINSTRUCTUREOFAUSTENITE;BSELECTEDAREAELECTRON

DIFFRACTIONPATTERNTAKENFROMREGION(A);CKEYPATTERN;DSTRUCTUREOFGRAINBOUNDARY;ESELECTED

AREAELECTRONDIFFRACTIONPATTERNTAKENFROMREGION(D);FKEYPATTERN;GSURFACEMARTENSITE

FIG.4.STRUCTUREOFAGEDAT350 STEELCR18NI2N1:AHOMOGENEOUSDECOMPOSITIONOFAUSTENITE;BSELECTED

AREAELECTRONDIFFRACTIONPATTERNTAKENFROMREGION(D);CKEYPATTERN;DEXTINCTIONCONTOURSANDMARTENSITE;ESELECTEDAREAELECTRONDIFFRACTIONPATTERNTAKENFROMREGION(D);FKEYPATTERN

Zone axis [ 433

]

e

a

313

133

000

422

220Zone axis [

111 ]

202

c

d

110 , 200Cr2N

211

321

310

020

121, 220Cr2N

Zone axis [

201 ]

Zone axis [001]Cr2N

Zone axis [ 131

]

fg

111

a b

111CrN111

200

200CrN

111 rN

200

200CrN

111

111 CrN

131 CrN

131

Zone axis [ 110

] CrN Zone axis [

101 ] CrN

c

000

d e

112

Zone axis [ 521

]

Zone axis [ 010

]Cr2N004

204

200113

202

321

112

Zone axis [

111 ]

Zone axis [113]

110131

000

f420 Zone axis [ 521

]


6/10


24

FIG. 5 STRUCTURE OF AGED AT 500 STEEL CR18NI2N1: A GRAIN BOUNDARY; B SELECTED-AREA ELECTRON DIFFRACTION

PATTERN TAKEN FROM REGION (A); C KEY PATTERN; D MARTENSITE ; E SELECTED-AREA ELECTRON DIFFRACTION PATTERNTAKEN FROM REGION (D); F KEY PATTERN

FIG. 6 STRUCTURE OF AGED AT 600 STEEL CR18NI2N1: GRAIN BOUNDARY; B SELECTED-AREA ELECTRON DIFFRACTION

PATTERN TAKEN FROM REGION (A); C KEY PATTERN

does not considerably increase the corrosion current

atSCCofironbutahighlevelofthem(tr)causes

a significant growth of this one (Fig. 8). And taking

intoconsiderationthesametodelayedfailure[18,19]

mechanism of SCC, when the main depolarization

process is hydrogen ions (H+) discharge on the

ordered clusters to atoms (H), they become the

effective sub micro cathodes in electrochemical

process on the surface of the steel. The atoms of

hydrogen can join to molecules (H2) significantly

increasing their size and level of stresses in the

clusters. That is why the stressmartensite can be

formedfromthoselocalareasofstructure.

After 24% reduction the austenite has more stabilitythan after 20% reductionbecause of strain recovery,

thats confirmedby dependence of micro hardnessfrom deformation degree (Fig.9). Fig. 10 shows the

structure of deformedbefore aging at 350 C steel

with the electron diffraction pattern where

martensitecanbenoted.

Zone axis [

101 ]

Zone axis [

811 ]

a b c

011, 110

211 200, 002

211

202

120

401000

Zone axis

[ 011

]

Zone axis [010]Cr2N

202

,

211

331

151

011

200

531

022

711

Zone axis [

101 ]

Zone axis

[

611 ]

000

d ef

a b c

200

011

211

110

203Cr2N, 112

222, 404Cr2N

Zone axis [ 110

]

Zone axis [ 011

]

102

Zone axis [ 010

]Cr2N

000


7/10


25

FIG.7.KINETICSOFELECTRICRESISTANCECHANGEININVESTIGATEDSTEELSCR21N1(1),CR18NI2N1(2) CR18C1(3)DURING

THEAGINGAT:A300;B400;C500

a

b

c


8/10


26

FIG.10STRUCTUREOFDEFORMEDATAN8%REDUCTIONBEFOREAGINGAT350 STEELCR18NI2N1: MARTENSITE;B

SELECTEDAREAELECTRONDIFFRACTIONPATTERNTAKENFROMREGION(A);CKEYPATTERN

FIG. 8 POLARIZATION DIAGRAM OF CORROSION AT SCC:

O2ABC CATHODE CURVE; FE/FE2+X11 AND FE/FE2+X22 ANODECURVESATADIFFERENTSTRESS

200

250

300

350

400

450

500

0 11 20 24

, %

HV100

FIG.9

DEPENDENCE

OF

THE

MICRO

HARDNESS

ON

THE

DEGREEOFCPDPRECEDEDTHEAGINGAT350 INSTEEL

CR18NI2N1

Treatment with CPD at 20% reduction after aging at

350Cisfoundtobemoreeffective:thecorrosionrate

decreasedbyanorderandthereductionofstrengthat

SCC was about a quarter of magnitudes of

undeformed state. This positive influence of CPD is

probably connected with breaking the order in

metastable clusters which could be acceptors of

discharged hydrogen and nucleus of stressinduced

martensiteatSCC.

Conclusion

The structure of quenched steels Cr21N1, Cr18Ni2N1

andCr18C1

with

high

content

of

nitrogen

and

carbon,

respectively 1.021, 0.899 and 0.920% consists of

metastable austenite with nitrides or carbides settled

downthegrainboundaries.Alsoasmallcontentof

phase takes place near the nitrides/carbides or as a

resultofpolishing.

Twostagesofdecompositionofausteniteattempering

were shown to be in nitrogen steels by electric

resistance: separation of the solid solution with

chromiumfollowedbyorderingoftheseclusterswith

nitrogenwhichinducedbytimeexposureorstresses.

The highest hardness, corrosion rate and stress

corrosion cracking susceptibility in HNS were

observed at the second stage of aging. This structural

state characterized of ordered enriched with

chromium and nitrogen clusters which had an ability

totransformintoastressinducedmartensite.

Coldplasticdeformationat812%reductionpreceding

the aging at 350 C is shown to decrease three times

thecorrosionrateofthesteelCr18Ni2N1ascompared

to the undeformed state. The role of CPD at this

degree consists of accelerating of nitrides CrNprecipitation without intermediate stage of ordering

i

-Fe/Fe2+

i1 i2

1 - tr

2 - tr

-O2

-H+/HA

B

Cx2

1

2

1

310

200

110, 020

002

222

220

113

000

Zone axis [100 ]

Zone axis [ 011

]

Zone axis [ 031

]

311

a b c


9/10


27

clusters. A thermoplastic treatmentby 20% CPD after

agingat350Cismoreeffectivebecauseofdestroying

already formed ordered clusters, which are the main

reasonofhighsusceptibilitytoSCC.

ACKNOWLEDGMENT

TheauthorwishestothankMansurS.Khadyevforhis

helpinexperimentalprocedure.

This work was carried out and is running now with

the financial support of Russian Foundation for Basic

Research,grantsN070300062aandN110300065.

REFERENCES

[1] Stein G., Hucklenbroich I. Manufacturing and

Applicationsof High NitrogenSteels.HNS2003.High

Nitrogen Steels. Editors: Markus O. Speidel, ClaudiaKowanda, Markus Diener. Zzich: Institute of

Metallurgy,SwissFederalInstituteofTechnology,ETH,

2003:2130.

[2] Speidel M. O., Mingling ZhengCui. HighNitrogen

AusteniticStainlessSteels.InthesamebookHNS2003:

6373.

[3] SvyazhinA.G.NitrogenofWidePurposes.Production,

Treatment,Properties.InthesamebookHNS2003:43

52.

[4] Hnnen H., Talonen J., Romu J. et al. Summary ofRecentReasearchonNAlloyingofSteelsinFinland.In

thesamebookHNS2003:3141.

[5] Dong Han, Lin Qizeng, Rong Fan et al. Development

and Applications of Nitrogen Alloyed Stainless Steels

inChina.InthesamebookHNS2003:5361.

[6] Saller G., Aigner H. High Nitrogen Alloyed Steels for

NonMagnetic Drill Collars. In the same book HNS

2003:129138.

[7] Gcmen Alkan. Development of high Nitrogen 12%

ChromiumSteelsforGasTurbineDiskApplications.InthesamebookHNS2003:113128.

[8] KIM Yong Hwan, KIM Kwang Yuk, LEE Yong Deuk.

NitrogenAlloyed,MetastableAusteniticStainlessSteel

for Automotive Structural Applications. In the same

bookHNS2003:149158.

[9] Colombie V., Montserrat X., Brown G. et al. Nitrogen

Alloyed Austenitic Stainless Steels for Wire and Cable

Applications.InthesamebookHNS2003:199210.

[10] Berezovskaya V. V., Kostina M. V., Blinov E. V., et al.

Corrosion Properties of Austenitic CrMnNiN Steelswith Various Manganese Concentration. Izv. Ross.

Akad. Nauk, Ser. Met., 2008, 1: 3641. [Russian

Metallurgy(Metally),2008,1:2933].

[11] Kostina M. V., Bannykh O. A., Blinov V. M.,

Berezovskaya V. V., et al. Effect of Chemical

Composition and Heat Treatment on the Corrosion

Properties in High Nitrigen IronBased AlloysContaining1524%Cr.Izv.Ross.Akad.Nauk,Ser.Met.,

2001, 3: 2634. [Russian Metallurgy (Metally), 2001, 3:

243250].

[12] Bannykh O. A., Berezovskaya V. V., Effect of heat

treatment conditions on the structure and

physicomechanical and chemical properties of an Ni

CrCuTi maraging steel. Izv. Ross. Akad. Nauk, Ser.

Met.,2007,3:4047.[RussianMetallurgy(Metally),vol.

2007,3:201208].

[13] Gorelik S. S., Skakov Yu. A., Rastorguev L. N. Xray

diffraction and electronoptical analyses. Moscow:

MISIS,2002.358pp.

[14] BannykhO.A.,BlinovV.M.,BerezovskayaV.V.,etal.

EffectoftheMartensiteTransformationinFeCrN

Alloys on Their Stress Corrosion Cracking. Izv. Ross.

Akad. Nauk, Ser. Met., 2005, 4: 2631. [Russian


[15] BerezovskayaV.V.,GolyakovI.V.,BannykhO.A.etal.

EffectofColdPlasticDeformationontheStructureand

Corrosion Resistance of Austenitic Aging 0Kh18N2A

Alloy. Izv. Ross. Akad. Nauk, Ser. Met., 2006, 5: 2932.[RussianMetallurgy(Metally),2006,5:390393].

[16] LivshitsB.G.,KraposhinV.S.,LinetskiyYa.L.Physical

PropertiesofMetals.Moscow:Metallurgiya,1980.320

pp.

[17] Isaev N. I. Theory of corrosion processes. Moscow:

Metallurgiya,1997.368pp.

[18] Nelson H. G., Williams D. P. Stress Corrosion and

Hydrogen Embrittlement of Iron Base Alloys //R.

StaehleandSpeidel,eds.1977:390404.

[19] BerezovskayaV. V.DelayedFailure of Maraging Steels

in Environment. Advances in Chemistry Research.

Volume 6. Editors: James C. Taylor.Chapter 7. N.Y.,

USA,NovaSciencePublishersInc.2011:219244.

Vera. V. Berezovskaya was born

04.04.1949.

Engineer, Physics of Metals, Ural

Polytechnic Institute (Sverdlovsk,

USSR),1971;

PhD,MetalScienceandHeatTreatment,


10/10


28

UralPolytechnicInstitute,1985;

Assoc. of Prof., Metallurgical Department of Ural State

Technical University, Yekaterinburg (former Ural

PolytechnicInstitute,Sverdlovsk),1996;

Doctorofscience,MetalScienceandHeatTreatment,Baikov

Institute of Metallurgy and Materials Science, RussianAcademyofScience,Moscow,Russia,2004;

Professor, Metallurgical Department of Ural State Technical

University,Yekaterinburg,2005;

Currently Professor, Institute of Metal Science and

Metallurgy of Ural Federal University named after the first

PresidentofRussiaB.N.Yeltsin.

The main area of scientific interest is relationshipbetween

structureandfractureofstainlessandhighstrengthsteelsat

cavitations,delayedfailureandstresscorrosioncracking.

She is a LECTURER at the Ural Federal University onfollowing subjects: Material Science; Theory of corrosion,

corrosionresistant materials and coatings, from 1991 and

Advanced Materials and Technologies from 2010. She has

about200publications,themainofthemare:

Berezovskaya V. V. Structural Factors Governing Steel

ResistanceduringOperationinCorrosiveMediaunder

Cavitation Conditions. Metallovedenie i Termicheskaya

ObrabotkaMetallov,1987,11:5056[MetalScienceandHeat

Treatment. 1987. V.29,I.1112:863869].

Berezovskaya V. V. Delayed Failure of Maraging Steels in

Environment. Advances in Chemistry Research. Volume 6.

Editors: James C. Taylor. Chapter 7. N.Y., USA, Nova

SciencePublishersInc.2011.219244.

Berezovskaya V. V., Savrai R. A., Merkushkin E. A.,

Makarov A. V. Structure and Mechanical Properties of newhighnitrogen CrMn Steels Containing Molybdenum. Izv.

Ross. Akad. Nauk, Ser. Met., 2012, 3: 3139. [Russian


Her current research interests lie in the area of High

Nitrogen Steels, their structure, mechanical, physical and

chemicalproperties.

Dr. Berezovskaya supervises the contracts and grants,

preparedtwoMasters(2010,2011)andthePhD(2002).Sheis

Member of New York Academy of Sciences (New York,

USA,1996);

Member of Association of Russian Metallurgists (Moscow,

Russia2002).

Shehas

Honorary title Hero of Labor of regional importance

(Sverdlovskayaarea,Russia,2003);

Diploma of the Ministry of Education and Science for her

significant contribution to the training of highly qualified

specialists(Russia,2011).

Date post:	08-Aug-2018
Category:	Documents
Upload:	sep-publisher
View:	217 times
Download:	0 times

Effect of Thermo‐Plastic Treatment on Structure and Corrosion Properties of High Nitrogen...

Documents