CA2012065A1 - Heat-deformable, ferritic steel alloy - Google Patents
Heat-deformable, ferritic steel alloyInfo
- Publication number
- CA2012065A1 CA2012065A1 CA002012065A CA2012065A CA2012065A1 CA 2012065 A1 CA2012065 A1 CA 2012065A1 CA 002012065 A CA002012065 A CA 002012065A CA 2012065 A CA2012065 A CA 2012065A CA 2012065 A1 CA2012065 A1 CA 2012065A1
- Authority
- CA
- Canada
- Prior art keywords
- alloy
- max
- titanium
- zirconium
- replaced
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Abandoned
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Powder Metallurgy (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Catalysts (AREA)
- Resistance Heating (AREA)
- Soft Magnetic Materials (AREA)
- Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
- Superconductors And Manufacturing Methods Therefor (AREA)
- Heat Treatment Of Steel (AREA)
- Laminated Bodies (AREA)
Abstract
ABSTRACT OF THE DISCLOSURE
A heat-deformable, ferritic steel alloy, comprise:
20 up to 25 % chromium 5 up to 8 % aluminum max. 0.01 % phosphorous max. 0.01 % magnesium max. 0.05 % manganese max. 0.005 % sulfur rest iron including unavoidable impurities, also 0.03 up to 0.08 % yttrium 0.004 up to 0.008 % nitrogen 0.020 up to 0.040 % carbon and a substantially equal parts of 0.035 up to 0.07 % titanium 0.035 up to 0.07 % zirconium wherein the sum of the contents of titanium and zirconium in percentage is 1.7 - 3.5 times greater than the sum of the contents of C and N in percentages.
A heat-deformable, ferritic steel alloy, comprise:
20 up to 25 % chromium 5 up to 8 % aluminum max. 0.01 % phosphorous max. 0.01 % magnesium max. 0.05 % manganese max. 0.005 % sulfur rest iron including unavoidable impurities, also 0.03 up to 0.08 % yttrium 0.004 up to 0.008 % nitrogen 0.020 up to 0.040 % carbon and a substantially equal parts of 0.035 up to 0.07 % titanium 0.035 up to 0.07 % zirconium wherein the sum of the contents of titanium and zirconium in percentage is 1.7 - 3.5 times greater than the sum of the contents of C and N in percentages.
Description
2 ~ ~ ~
BACKG~O~ND OF TH~ INVENTXON
The present in~ention relates to ~ heat-deformable, ~erri~ia steel ~lloy More particularly, i~ xel~tes to such a steel alloy which ha~ the ollowing elements:
20 ~p to 25 ~ chro~ium S up to 8 ~ alum~num ma~. Q.01 ~ pho~phor max. 0.01 ~ ~agnésium max. O.S % manganPse max. O.Q0~ ~ sul~ur rest ixon including unavoidable impurities.
Allcys of the above mentio~ed general~:~ype ar~
known in th~ art and utili~d for producin~ electrlcal heating elem~n~s and catalys~ carrier ~o~ hi~h ~hermal strength. The~
~orm highly adhesi~e oxide layers and pos~es~a ver~ good non-scaling stren~th~ So~e attempts~bave bee~made to furtner improve the ba~ic oomposi~tion b~ ~the; addit}on of further elements:or by the reducti~on o~ u~avoidablq impuxlties ~aused by ma~uac~uring. :~
Fo~:example, the BritiBh documen~;~G~-A~2 07Q 642 propose to add up to 2~ yt~rium, hafnium, zirconium, ce~ium or lanthanu~ a~ well a~ O.l to~2~ anium~or:~maki~g ine ~ain~caqt structure and;improving the~ heat~de~ormability.
~he addi~ion o~yt~rlum, ha~ium, zirconium and mixing metal~
:::
} (CE ~ ~a) amou~ted ~or ex~mple respecLively ~p t~ 1% a~
de~ined in s1aims 7, 8, lO and ll of this reference. ~he best results were obtained wi~h 0.34~ ~i and 0.46~ Nb in the ~xanlple ~. It has howeve~ been recognized ~ha~ the te~ching of t~is ~e~rence is connected with cextain disadvantages.
Tak~ng into co3l~idexation ~hat the several propos~d admixtu~s are very e~pensi~e and at ~xactions a~ up to 1~
the efficien~ of ~he steel alloy is conside~a~l~ influenced, deterrnined that the titanium in the described ~u~ntitt~
pxovides ~or an imp~ovement or th~ mechanical properties, ~nd imul~neously worse~s ~owever ~he behavio~ und~r cyc~ically a.lter~tin~ oxidation conditions. The serviCe life sinks in VIW-test from 5 ~ O oo cycl ic c~ang~ ~or the tita~iu~-~ree probe to 2,800 ~clic chan~es ~o~ ~he comparable probe ~ith 1~ 0.~7% of titanium. ~his is co~nected with the enrichment o~
titanium ox3.de in the outeX oxide layer, whi~h ~auses a chipping o~f o~ the oxlde: iayer (compare ~orxosion Sienae, Vol, 24, No. 7, l98~, pp~ 613-627).
During ~he al~ove montioned ~7IW tes~ smaI l t~s~ing coils o~ wire With ~hic!~ness 5f 0 . 4 run a~e ~heated by ~he direct ~ passage o~ air. ~e ~lo~ supply is turned Oll:
~d turned of in continuoug exchange or 2 mlnutes each. :~
The aahieved ma~imurn tempera~ure is optical ly measured and :
tho s~me switching frequency ma1n~ained constant~ by change o4 the applied voltage duri~g th~ wbo1~ tes~ing ~tlme. It is~
~.
BACKG~O~ND OF TH~ INVENTXON
The present in~ention relates to ~ heat-deformable, ~erri~ia steel ~lloy More particularly, i~ xel~tes to such a steel alloy which ha~ the ollowing elements:
20 ~p to 25 ~ chro~ium S up to 8 ~ alum~num ma~. Q.01 ~ pho~phor max. 0.01 ~ ~agnésium max. O.S % manganPse max. O.Q0~ ~ sul~ur rest ixon including unavoidable impurities.
Allcys of the above mentio~ed general~:~ype ar~
known in th~ art and utili~d for producin~ electrlcal heating elem~n~s and catalys~ carrier ~o~ hi~h ~hermal strength. The~
~orm highly adhesi~e oxide layers and pos~es~a ver~ good non-scaling stren~th~ So~e attempts~bave bee~made to furtner improve the ba~ic oomposi~tion b~ ~the; addit}on of further elements:or by the reducti~on o~ u~avoidablq impuxlties ~aused by ma~uac~uring. :~
Fo~:example, the BritiBh documen~;~G~-A~2 07Q 642 propose to add up to 2~ yt~rium, hafnium, zirconium, ce~ium or lanthanu~ a~ well a~ O.l to~2~ anium~or:~maki~g ine ~ain~caqt structure and;improving the~ heat~de~ormability.
~he addi~ion o~yt~rlum, ha~ium, zirconium and mixing metal~
:::
} (CE ~ ~a) amou~ted ~or ex~mple respecLively ~p t~ 1% a~
de~ined in s1aims 7, 8, lO and ll of this reference. ~he best results were obtained wi~h 0.34~ ~i and 0.46~ Nb in the ~xanlple ~. It has howeve~ been recognized ~ha~ the te~ching of t~is ~e~rence is connected with cextain disadvantages.
Tak~ng into co3l~idexation ~hat the several propos~d admixtu~s are very e~pensi~e and at ~xactions a~ up to 1~
the efficien~ of ~he steel alloy is conside~a~l~ influenced, deterrnined that the titanium in the described ~u~ntitt~
pxovides ~or an imp~ovement or th~ mechanical properties, ~nd imul~neously worse~s ~owever ~he behavio~ und~r cyc~ically a.lter~tin~ oxidation conditions. The serviCe life sinks in VIW-test from 5 ~ O oo cycl ic c~ang~ ~or the tita~iu~-~ree probe to 2,800 ~clic chan~es ~o~ ~he comparable probe ~ith 1~ 0.~7% of titanium. ~his is co~nected with the enrichment o~
titanium ox3.de in the outeX oxide layer, whi~h ~auses a chipping o~f o~ the oxlde: iayer (compare ~orxosion Sienae, Vol, 24, No. 7, l98~, pp~ 613-627).
During ~he al~ove montioned ~7IW tes~ smaI l t~s~ing coils o~ wire With ~hic!~ness 5f 0 . 4 run a~e ~heated by ~he direct ~ passage o~ air. ~e ~lo~ supply is turned Oll:
~d turned of in continuoug exchange or 2 mlnutes each. :~
The aahieved ma~imurn tempera~ure is optical ly measured and :
tho s~me switching frequency ma1n~ained constant~ by change o4 the applied voltage duri~g th~ wbo1~ tes~ing ~tlme. It is~
~.
-3~
, , . ,.. . .. " .... .,.. . , , .. ,,, ,. ., . , . , , ~ , ,, . .
, : . :: . --, , :, , ~ . , ~
, ai~closed in K.E. Volk: N~ckel u~d Nickellegierungen, pg. 145, Springex-Verlag, 1970.
Moreover, ~or a probe of 0.47~ Ti in the heat de~ormation ~tage strong, non-uniformly distriblted titanium c~rbide d~rect~ wer~ obse~ved~ They xesul~ in si~ificantl~
different mechani~al properties ~nd make the uniforrn cold deformation di~ ~icult or impo~:~ible .
The a~dition o~ niobium causes in ferritic ~-Cr-allo~s not only a ~light i~Crease in 475C imb~ leness (compa~e bo~on, calcium, colombium and zirconiurn in ~xon and Steel, pg. lg9, ~ohn WIley & Sonsr~Nq~r York, 1966, but al~o worsens the st~ength under cyclically alternating oxidation condition~. With increasi~g temp~r~t~ra vari~ous niodium oxides are produced ~Nb, NbO2, Nb2O5~ which ls connec~ed With volume increase, g~rowth stxeSSes an~d resulting oxide chipping :
o~. Moreove~, the ~ hi~h t~mperature ver~ion of ~he niodium oxi~e is no~ ver~ stabl~ ince its~melting~poin~ i9 rela~ively lCw, such~as~for~example:approximately 1,500C
(compare P. ~o~,tad: iIigh ~emp-ratu~e O~id~ation of M~tal~ r~
page 215, ~ohn Wil~y 6 Sons, N~w York,~1966). ~ ;
Th~ ~basic alloy in accoxdance with the ~uropea:n Paten~ ~ooument EP-B-O 091 526 cont~inJ in addition to o.O:02~
C.O~ o~ ~are e~rth~ and maximum 0.04~ phosp~Lo~ous ~nd 0 .03~ ~ :
~ul~ux, ~ also alrconium and Aicbi~ fcr~ atabilLzatlon and imprcvement ci tl ~ iatigue strength,~ Zr and ~Nb must~he dded~
~; --in dependence upon the cont~n-~ o carbon (maximal 0.05~) and nitrogen ~ma~imum 0.05~) up to 0.068 - 1,9~ and always up ~o 0.364 or 1.209~ Nb when carbon and nitxogen musk b2 completely absent (see E~ample 1 ) .
Steel allo~s in accordance with this reference also nave disadvar~t~ges, A~; long as xa~e earth arP add~d it is necessary ~o l:ake in~o account the orma~ion o~ rel~ti~
low melting oxide.q, s~ that the ~teel alloy ca~ be used only or p~edetPrmined ma2~imurn temperatures. Also phosphorous ~onterlt up to 0 . 04~ and s~ u~ conten up to 0. 03~ are not tol~r~ble in ac~ordance with the ~etermination of the ~pplicant. Especially wi~h the zirconium content up to app~o~imately 1~ and the niobium c~ntent up to appro:cimat~ly 2g~ signi' iC~llt di~advantages must ~e ~aken into conside~ation.
Fo~ nioblum ~hey axe the s~rne as in ~he Gexman r~ference GB~ 2 070 642. Wi~h higher ~i~ooniu~m conterlt i~c~ease~ ~he improvemenl: of the cxidation streng~h very fast and runs into oppo~l e ~H. P~ei~fer:and H. Thomas: Oxid~tiorl ~es ani:
Alloys, paye~260, Springer-Verla~g~ 1963)~ Moreo~erj with the zirconium content whiah lies ~ar a~ove the dissolutio~
propexty ox ~er~itic Fe-matrix, ~oarsely~dlspersed separation o~ zirconium ~itrides, ca~bide~ and~ carbonltrides :o~cur, whi~h cause no dis~dvantageous stoppage of the grain growth and no si~nlficant st~ength in~reaee~
S M~A~Y OF THE IN~IENTION
~ccordingly, it i~ an object o~ the pre3ent invex~tion to p~otti~e a heat-de~o~mable, ~errit:i~ s~eel ~1 loy which ~urther i~proves the known basic alloy and avoid t:he S disadvantage~ Qf~ the prior ~rt.
~oxe particularly, 1t is a~ object o~ the present in~en~ion to pr~vide ~uch an al loy in which ~he grain grow~h is signi~icantly limited and the service life in c~clical oxidation te~t is significan~ly improved.
In ~eeping wit:h these objects aIld with o~her~ whlch will become apparen~ h~reina~qr, one ~ea~slr~ of the p~esent inv~ntion resides, ~riefly ~tated, in khe allo~ whi~h comp~ises:
ao up ~o 25 ~ ~ ch~omium 5 up to 8 ~ alwninum :
max. 0.01 ~ phosphorous ~ : ~
.:
max. 0.û1 ~ ;magnesium ~ :
max. 0.5 ~ mangan~se max~. 0 .005 ~ ~ sulfur ~ ;
2~ : ~est iron including unavoidable impurities,~ a1so :
0.03 up~ ~o 0.0~ ~ y~t~ium 0.00~4 u~ to 0.008~ % nit~ogen~
0.020 u~ to 0~0~0 ~ c~rbon ~5 and a subata~tially: equal parts~ o~
.
~ .
.. ,. . . ' ' :
'' . , . ~ ~
2 ~
1 0.035 up to 0.~7 ~ ~itaniu~
0~035 up to 0.07 ~ zirconiu~
whexein the su~ o~ the con~en~s o~ titanium and zirconiu~ in pe~centages is 1.75 - 3.5 tinle~ grea~er t~an ~he ~um of the content~ o~ ~ and N in percentag~s.
When the alloy i~ formed in accordance with these f eatures it improv~s the ~on-basic alloys and eliminate~
t~e di~advantases o~ t~e ~rior art.
In accordance wi~h ano~her ~eature of ~he presen~
invention, the ratio o~ the admi~tuxes o~ ti~anlum and ~irconium lie in ~he region between 0.6 and 1,~.
~ is still another ~eat~re o~ present invention that titanium and irconium completely or partially replaced with ha~nium and~o~:~antalum or ~na~ium.
In~acco~dance with a ~urkher eature:p~ the pre~ent:
invention, a~ least two element~ Ti, Zr, ~f,~Ta and V are replaced. : ~ ~
Finally, it is ~till~ a further fea~ure of the pre~ent invention that three o~ the above mentio~ed elements can be replaaed.
Th~ novel :~eatures whi~h a~e`con~idered as ~;
charact~ristic ~or the in~ention~are~set~o~tn :in par~icula~
in the appended claims~. The~invention~ltael~, however, both :~:
as ~o i~ c~n~truction and i~s m~ethod~ o~ op~ra~ion:,~ together ~5 with additional objects and :adva~tag~s ~here~ wi~il be: be~:t :-7~
~:
und~rs~ood ~r~7m the following descxiption o~ specific em~odiments when read in conllection with the accornpanying drawings.
B~IEF ~SCRIP~ON OP TSE DR~WINGS
FI~. la and ~b are ~riews showing 'che used testing device in a simpli~ied manner;
FIG. 2 i; a view showing the achieved ~alues of ~er~iae 1 i~e;
FXG. 3 i~ a view showing the achi~eved values o~
10thermal stre~th; ~ ;
FIG. 4 is a view ~howing the a~hie~red ~ralues of servi~e li~e under~ pull ing loa~;
FIGS. :5a and 5b ~show values ~for ~the~ grain grow~
or ~or the bending r~umbera.
.
: , 2~12~
~ESC~XPTION OF THE PREFERR~D ~MBODIL~E~TS
__ __~___ In accorda~ce ~i~h the present invention, a heat-deformable, ferritic steel ~lloy is proposed with the f o~lowing c~mposition:
20 up to 25 ~ chromium 5 Up to ~ % al~lminum max. 0,01 ~ phasphorous max. 0.01 ~ magnesium max. 0.5 ~ manganes~
max. 0~005 ~ sul~ur re~t iron including una~oidable impu~i~ies, also 0,03 up to 0.08 ~ y~trium . 0.004 up to 0.008 ~ nltrogen 0,020 up ~o 0~040 ~ aarbon ~nd a ~ub tantiall~equal parts of ~
0,035 u~to 0,07 b titanium Q.035 up~:~o 0~07 ~ ~ixaonium : : ~
wherein the sum o:~he contents~;o~ itanium ~nd zi~co~ium in perce~tage~ i~:1.75 - 3.5 times ~r~ater~:than the 1lm o~ the contents o~ C and N :irl percent~ges, ~
::
The ratio o~ tne; admixture~ of tita~lum and zirco~iu~ can lie in the~;reqi~on~of 0~ - 0:.4.~
It i~;also p~s~sible~to replace~ tit~anlum~or zlxconium completely or partially by ha~nium~and/ox~tantalum ~o~
~:
' ~ 21~
vanadium. It i5 ~lso po~sible to replace at l~ast t~ro elernent~ Ti~ Zx, H, Ta and V. Fur~hermore, it i~ also pos~ible to re~lace at l~ast three o~ the above ~entioned elemen~s .
A davice for testing the ser~lc~ e or a hori~ontally arra.~ged, helically wound hea~ing conduc~or 1 is shown in FXG. la. ~he heatin~ conduct~r 1 is clamped at its one side i~ a holder 2 and c~onr~ected ~i~h a voltage sollrce 3, In this ca~e ~he hea~ing conductor 1 i s compo~ed of a coil with len~th 50 mm with 12 con~olution~ and an inxlex diameter o~ 3 ~m, ~rhe diametex of wi:re amounts to O . 4:: mm. ~he heating conduc~or was turned o~ and:turned of~ al~erna~in~ly ever~
2 minutes. ~ radiation pyxometer was measu~ing the tempe~
ratuxe reached durir~ ~he: heating phase in a contactless -manner and regulated ~by a chan~e~o~the applied ~oltage to a corl~ tant ~7a lue .
Such tests ~exe conducted in rlornal air atmo~phere up to throughburning of the hea~ing conductor~. The~ numbe~
o~ the ~cles ~?xoduced a dir~ct value or the service li:~e. ~or all materials: unavoidable, more or ies~ s~xong~oxida~ion lead~ to the ~ac~ th~t the metal lic cro~s-seation a~ailable~
for aonducting the ~eleo~rical c~xre~t ~becom~s~ smaller a~ter :
elapsing the ~lme. ~here~ore, t~e eleotrioal re;sistance ;
correspondingly~ increases~and a~predetermined :te~tlng~
temperatu~e~ ~àll~:be maintained only~with; unchanyed ~ hing :: : : ~ :
;
: -10~
:
- . ,,. ; ~ . - ,. . ~ :
1 xhythm when the voltage is increased. ~he utilized testing apparatus i~ an ~utoma~ically ope~ating temperature regulating device. Therefore~ the ~esti~g t~mp~ratu~e pro~ided ~or the heati~g phase can be main~ained th~ough the entire testing time up to the ~hroughburning independently o the prog~essing o~idation o~ ~he ~eatin~ conduct~x.
Xn the devi~e ~or te~ting the Se~ice life of a vertically suspended hea~ing conducto~ Wire ~ shown in FIG, lb, the heating conductor wire ha he length o~ 1 meter.
It is clamped on its Upper end in a holdeir 5~ loaded With a ~ariable weight 6~ and connec~ed with a volta~e Source 7.
In thi~ device the heating conducto~ wire with a thickness of 0.4 mm is turned on and turned Of L- alternatingly every 2 ~inu~e~. ~ere also as in the arXan~ement o~ FIG~ la, the temperature achieved duxing ~he heatin~ phase wa~
measured iIl a contactless m~nner and regulated to a cons~a.nt ~ralue.
The resul~ presen~ed in FIGS~ ~ - 5 show a comparisa~ alloy ~prob~ 1) and an inven~ive mGdi~:led alloy 2 0 (probe 2 ) wlth khe ol lowiny comp~osition:
:: :
--11-- :
. .:, ~ ~ jC~
1 Probe 1 Probe 2 _ . . _ ~ .
Cr 20.10 20.4S
1 5.05 P O.OOg 9~007 M~ 0.01 0.01 ~n Q.22 0.15 S 0.00~ 0.00~ ~:
y ~ ~.04 ~ 0.010 0,007 10 C 0.04S 0.037 Ti 0 . 01 Zr : 0,16 ~0.06 Fe rest ~e :
~XG. 2 shows he servic~ li e ~alues achie~ed in : .
lS the device in accordance ~ith FIG~. 1a represen~ed by~the number c~ cyles ~il throughburn m g.~ ~he~p~obés w~re~;~urned ':
on and of~ ~very 2 minut~sj:and ~he~t~peratu~re ~eached:during the h~ating phase Ls measu;red~in:~a~contactlesa manner~and~
applied voltage was changed so that; durlng ~th~ total te~ting :.
time in each ~y~cle a consta~t testing:temper~ure o~ 1200:C
~: :
was maintai~ed. Th~ probe 1 withs~o~d:5~3~;3 c~cle~ while~th probe 2 was burned:fi~st ~er:6213 cycle~ his coxxespond~d:~
to an incxease ~f o~er 15~
~In ~IG. 3~he determin~d~:~thermal::str~eng~h~;were ~h~wn, a~d l~ aan be.3een~tha~:~he~ invent1ve mo~i~ied~alloy ~:;
1 has highe~ therm21 strengths value in the total tempera~ure tes~ing region.
FIG. 4 shows the achieved c~cle numbe~ during ~esting in ~ccordance wi~ FIG. ~b in d~pendence on ~he S ~pplied voltage. ~he modi~ied alloy ~howed at all load~ a significantly higher ser~rice li~e. At a ~ol~aye o~ 2 N/~m2 the 6-t~rne, ~ t}le ~oltage 3 N/rnm3 appro~:imately 5-~ime, and ~t ~he volt~ge ~ N/mm2 always 3.5-ti~e increa3e in t~e ser~ice liLe was achieved.
~l~o the ductili~y of a material duxin~ a long time use ~t high temperatures is an important ~truatural ~eatu~e.
The xeduc~ion of the duc~ility ~ n ~erriLia Fe-Cr-~l-al loys d~als wikh a 3trong gr~in grow~h at hig~ ~emE~eratuxes. In FIG. Sa the gxain size ~alues are px~sented ~or the probe a~ter ~ . 5 day~ stor~ge at ~50-1050C, in um ~upper curve ) .
More~ver, the ~ain si~e v~lues ~or the modifi~d al lo~ a~ter ~:
ato~:age time or 13 days a~ 950, 10~0 and 1150C are shown :
~ e~ curv~. -It can be 3een th~ the mQdified allo~ at the double s~oxa~e time has considerably more fine grain ~0 st~uc~ure than ~he co~parison alloy.
.
~ t~i~ there~ore not surpri~in~ that the bending numbers ~num~er o4 the k~ndings by 1~0 to ~reakag~ in accordance with ~IG. 5b is co~siderabl~ hi~her ~or ~he inven~ive modified alloy due o:its ~ine grain~tructure, ~5 than in the~so~parls~n alloy ~or:~e p~obe~ s ored during 13 3- ~
: ~-: ' ' ~:
, .
: ~
2 ~
o~ ~.5 d~y~ at temperatu~es 950, 1075 and 1175~C. l~h~
comparison shows that the mo~iied allo~ h~s a significantl~f hi~her ductili~y ~han the comparison allo~.
It will b~ unders~ood ~hat each o the elements des~ribed ~bo~e, or ~o or more ~oge~her, may also ~ind a use~ul applicatiorL in other types o con~txucti~ns dif~erin~
from the types desc~ibed above, While the iI~Vention has ~een il lus~ated ~nd desaribed as en~bodie~ in a heat de~crmable, ~rritio st~el al loy, it is rlot intended to k,e lirnited to the details s~own, since v~ious modiica~ions and a~ructural char~ges maY be made wi thout dapartin~ in any way from th~ spirit of l:he pre ent inv~ntion.
Withou~ furth~ anal~sis, :the foregoing will so fully reveaI the g~ist o~ t he present invention ~ha~ others can, by a~plyinq ou~rent ~owledge, readily adap~ it for va~ious applica~ic)ns without ~omitting ~atures ~hatj fro~ th2 st-andpoint o~ prlor a~t, ~alrly cons~itute ~ ess~ntial characte~igtics o the g~enerLC or speciic aspe~ts o~ this 2 0 inv~ntion .
What is claimed a3 new and~ dèslxed to be protected by Lette~s Paten~ ~s ~et ~forth in the ~appended cla~ims.
:
. ~
`: ~ :
-14- : :
~` . ' . '
, , . ,.. . .. " .... .,.. . , , .. ,,, ,. ., . , . , , ~ , ,, . .
, : . :: . --, , :, , ~ . , ~
, ai~closed in K.E. Volk: N~ckel u~d Nickellegierungen, pg. 145, Springex-Verlag, 1970.
Moreover, ~or a probe of 0.47~ Ti in the heat de~ormation ~tage strong, non-uniformly distriblted titanium c~rbide d~rect~ wer~ obse~ved~ They xesul~ in si~ificantl~
different mechani~al properties ~nd make the uniforrn cold deformation di~ ~icult or impo~:~ible .
The a~dition o~ niobium causes in ferritic ~-Cr-allo~s not only a ~light i~Crease in 475C imb~ leness (compa~e bo~on, calcium, colombium and zirconiurn in ~xon and Steel, pg. lg9, ~ohn WIley & Sonsr~Nq~r York, 1966, but al~o worsens the st~ength under cyclically alternating oxidation condition~. With increasi~g temp~r~t~ra vari~ous niodium oxides are produced ~Nb, NbO2, Nb2O5~ which ls connec~ed With volume increase, g~rowth stxeSSes an~d resulting oxide chipping :
o~. Moreove~, the ~ hi~h t~mperature ver~ion of ~he niodium oxi~e is no~ ver~ stabl~ ince its~melting~poin~ i9 rela~ively lCw, such~as~for~example:approximately 1,500C
(compare P. ~o~,tad: iIigh ~emp-ratu~e O~id~ation of M~tal~ r~
page 215, ~ohn Wil~y 6 Sons, N~w York,~1966). ~ ;
Th~ ~basic alloy in accoxdance with the ~uropea:n Paten~ ~ooument EP-B-O 091 526 cont~inJ in addition to o.O:02~
C.O~ o~ ~are e~rth~ and maximum 0.04~ phosp~Lo~ous ~nd 0 .03~ ~ :
~ul~ux, ~ also alrconium and Aicbi~ fcr~ atabilLzatlon and imprcvement ci tl ~ iatigue strength,~ Zr and ~Nb must~he dded~
~; --in dependence upon the cont~n-~ o carbon (maximal 0.05~) and nitrogen ~ma~imum 0.05~) up to 0.068 - 1,9~ and always up ~o 0.364 or 1.209~ Nb when carbon and nitxogen musk b2 completely absent (see E~ample 1 ) .
Steel allo~s in accordance with this reference also nave disadvar~t~ges, A~; long as xa~e earth arP add~d it is necessary ~o l:ake in~o account the orma~ion o~ rel~ti~
low melting oxide.q, s~ that the ~teel alloy ca~ be used only or p~edetPrmined ma2~imurn temperatures. Also phosphorous ~onterlt up to 0 . 04~ and s~ u~ conten up to 0. 03~ are not tol~r~ble in ac~ordance with the ~etermination of the ~pplicant. Especially wi~h the zirconium content up to app~o~imately 1~ and the niobium c~ntent up to appro:cimat~ly 2g~ signi' iC~llt di~advantages must ~e ~aken into conside~ation.
Fo~ nioblum ~hey axe the s~rne as in ~he Gexman r~ference GB~ 2 070 642. Wi~h higher ~i~ooniu~m conterlt i~c~ease~ ~he improvemenl: of the cxidation streng~h very fast and runs into oppo~l e ~H. P~ei~fer:and H. Thomas: Oxid~tiorl ~es ani:
Alloys, paye~260, Springer-Verla~g~ 1963)~ Moreo~erj with the zirconium content whiah lies ~ar a~ove the dissolutio~
propexty ox ~er~itic Fe-matrix, ~oarsely~dlspersed separation o~ zirconium ~itrides, ca~bide~ and~ carbonltrides :o~cur, whi~h cause no dis~dvantageous stoppage of the grain growth and no si~nlficant st~ength in~reaee~
S M~A~Y OF THE IN~IENTION
~ccordingly, it i~ an object o~ the pre3ent invex~tion to p~otti~e a heat-de~o~mable, ~errit:i~ s~eel ~1 loy which ~urther i~proves the known basic alloy and avoid t:he S disadvantage~ Qf~ the prior ~rt.
~oxe particularly, 1t is a~ object o~ the present in~en~ion to pr~vide ~uch an al loy in which ~he grain grow~h is signi~icantly limited and the service life in c~clical oxidation te~t is significan~ly improved.
In ~eeping wit:h these objects aIld with o~her~ whlch will become apparen~ h~reina~qr, one ~ea~slr~ of the p~esent inv~ntion resides, ~riefly ~tated, in khe allo~ whi~h comp~ises:
ao up ~o 25 ~ ~ ch~omium 5 up to 8 ~ alwninum :
max. 0.01 ~ phosphorous ~ : ~
.:
max. 0.û1 ~ ;magnesium ~ :
max. 0.5 ~ mangan~se max~. 0 .005 ~ ~ sulfur ~ ;
2~ : ~est iron including unavoidable impurities,~ a1so :
0.03 up~ ~o 0.0~ ~ y~t~ium 0.00~4 u~ to 0.008~ % nit~ogen~
0.020 u~ to 0~0~0 ~ c~rbon ~5 and a subata~tially: equal parts~ o~
.
~ .
.. ,. . . ' ' :
'' . , . ~ ~
2 ~
1 0.035 up to 0.~7 ~ ~itaniu~
0~035 up to 0.07 ~ zirconiu~
whexein the su~ o~ the con~en~s o~ titanium and zirconiu~ in pe~centages is 1.75 - 3.5 tinle~ grea~er t~an ~he ~um of the content~ o~ ~ and N in percentag~s.
When the alloy i~ formed in accordance with these f eatures it improv~s the ~on-basic alloys and eliminate~
t~e di~advantases o~ t~e ~rior art.
In accordance wi~h ano~her ~eature of ~he presen~
invention, the ratio o~ the admi~tuxes o~ ti~anlum and ~irconium lie in ~he region between 0.6 and 1,~.
~ is still another ~eat~re o~ present invention that titanium and irconium completely or partially replaced with ha~nium and~o~:~antalum or ~na~ium.
In~acco~dance with a ~urkher eature:p~ the pre~ent:
invention, a~ least two element~ Ti, Zr, ~f,~Ta and V are replaced. : ~ ~
Finally, it is ~till~ a further fea~ure of the pre~ent invention that three o~ the above mentio~ed elements can be replaaed.
Th~ novel :~eatures whi~h a~e`con~idered as ~;
charact~ristic ~or the in~ention~are~set~o~tn :in par~icula~
in the appended claims~. The~invention~ltael~, however, both :~:
as ~o i~ c~n~truction and i~s m~ethod~ o~ op~ra~ion:,~ together ~5 with additional objects and :adva~tag~s ~here~ wi~il be: be~:t :-7~
~:
und~rs~ood ~r~7m the following descxiption o~ specific em~odiments when read in conllection with the accornpanying drawings.
B~IEF ~SCRIP~ON OP TSE DR~WINGS
FI~. la and ~b are ~riews showing 'che used testing device in a simpli~ied manner;
FIG. 2 i; a view showing the achieved ~alues of ~er~iae 1 i~e;
FXG. 3 i~ a view showing the achi~eved values o~
10thermal stre~th; ~ ;
FIG. 4 is a view ~howing the a~hie~red ~ralues of servi~e li~e under~ pull ing loa~;
FIGS. :5a and 5b ~show values ~for ~the~ grain grow~
or ~or the bending r~umbera.
.
: , 2~12~
~ESC~XPTION OF THE PREFERR~D ~MBODIL~E~TS
__ __~___ In accorda~ce ~i~h the present invention, a heat-deformable, ferritic steel ~lloy is proposed with the f o~lowing c~mposition:
20 up to 25 ~ chromium 5 Up to ~ % al~lminum max. 0,01 ~ phasphorous max. 0.01 ~ magnesium max. 0.5 ~ manganes~
max. 0~005 ~ sul~ur re~t iron including una~oidable impu~i~ies, also 0,03 up to 0.08 ~ y~trium . 0.004 up to 0.008 ~ nltrogen 0,020 up ~o 0~040 ~ aarbon ~nd a ~ub tantiall~equal parts of ~
0,035 u~to 0,07 b titanium Q.035 up~:~o 0~07 ~ ~ixaonium : : ~
wherein the sum o:~he contents~;o~ itanium ~nd zi~co~ium in perce~tage~ i~:1.75 - 3.5 times ~r~ater~:than the 1lm o~ the contents o~ C and N :irl percent~ges, ~
::
The ratio o~ tne; admixture~ of tita~lum and zirco~iu~ can lie in the~;reqi~on~of 0~ - 0:.4.~
It i~;also p~s~sible~to replace~ tit~anlum~or zlxconium completely or partially by ha~nium~and/ox~tantalum ~o~
~:
' ~ 21~
vanadium. It i5 ~lso po~sible to replace at l~ast t~ro elernent~ Ti~ Zx, H, Ta and V. Fur~hermore, it i~ also pos~ible to re~lace at l~ast three o~ the above ~entioned elemen~s .
A davice for testing the ser~lc~ e or a hori~ontally arra.~ged, helically wound hea~ing conduc~or 1 is shown in FXG. la. ~he heatin~ conduct~r 1 is clamped at its one side i~ a holder 2 and c~onr~ected ~i~h a voltage sollrce 3, In this ca~e ~he hea~ing conductor 1 i s compo~ed of a coil with len~th 50 mm with 12 con~olution~ and an inxlex diameter o~ 3 ~m, ~rhe diametex of wi:re amounts to O . 4:: mm. ~he heating conduc~or was turned o~ and:turned of~ al~erna~in~ly ever~
2 minutes. ~ radiation pyxometer was measu~ing the tempe~
ratuxe reached durir~ ~he: heating phase in a contactless -manner and regulated ~by a chan~e~o~the applied ~oltage to a corl~ tant ~7a lue .
Such tests ~exe conducted in rlornal air atmo~phere up to throughburning of the hea~ing conductor~. The~ numbe~
o~ the ~cles ~?xoduced a dir~ct value or the service li:~e. ~or all materials: unavoidable, more or ies~ s~xong~oxida~ion lead~ to the ~ac~ th~t the metal lic cro~s-seation a~ailable~
for aonducting the ~eleo~rical c~xre~t ~becom~s~ smaller a~ter :
elapsing the ~lme. ~here~ore, t~e eleotrioal re;sistance ;
correspondingly~ increases~and a~predetermined :te~tlng~
temperatu~e~ ~àll~:be maintained only~with; unchanyed ~ hing :: : : ~ :
;
: -10~
:
- . ,,. ; ~ . - ,. . ~ :
1 xhythm when the voltage is increased. ~he utilized testing apparatus i~ an ~utoma~ically ope~ating temperature regulating device. Therefore~ the ~esti~g t~mp~ratu~e pro~ided ~or the heati~g phase can be main~ained th~ough the entire testing time up to the ~hroughburning independently o the prog~essing o~idation o~ ~he ~eatin~ conduct~x.
Xn the devi~e ~or te~ting the Se~ice life of a vertically suspended hea~ing conducto~ Wire ~ shown in FIG, lb, the heating conductor wire ha he length o~ 1 meter.
It is clamped on its Upper end in a holdeir 5~ loaded With a ~ariable weight 6~ and connec~ed with a volta~e Source 7.
In thi~ device the heating conducto~ wire with a thickness of 0.4 mm is turned on and turned Of L- alternatingly every 2 ~inu~e~. ~ere also as in the arXan~ement o~ FIG~ la, the temperature achieved duxing ~he heatin~ phase wa~
measured iIl a contactless m~nner and regulated to a cons~a.nt ~ralue.
The resul~ presen~ed in FIGS~ ~ - 5 show a comparisa~ alloy ~prob~ 1) and an inven~ive mGdi~:led alloy 2 0 (probe 2 ) wlth khe ol lowiny comp~osition:
:: :
--11-- :
. .:, ~ ~ jC~
1 Probe 1 Probe 2 _ . . _ ~ .
Cr 20.10 20.4S
1 5.05 P O.OOg 9~007 M~ 0.01 0.01 ~n Q.22 0.15 S 0.00~ 0.00~ ~:
y ~ ~.04 ~ 0.010 0,007 10 C 0.04S 0.037 Ti 0 . 01 Zr : 0,16 ~0.06 Fe rest ~e :
~XG. 2 shows he servic~ li e ~alues achie~ed in : .
lS the device in accordance ~ith FIG~. 1a represen~ed by~the number c~ cyles ~il throughburn m g.~ ~he~p~obés w~re~;~urned ':
on and of~ ~very 2 minut~sj:and ~he~t~peratu~re ~eached:during the h~ating phase Ls measu;red~in:~a~contactlesa manner~and~
applied voltage was changed so that; durlng ~th~ total te~ting :.
time in each ~y~cle a consta~t testing:temper~ure o~ 1200:C
~: :
was maintai~ed. Th~ probe 1 withs~o~d:5~3~;3 c~cle~ while~th probe 2 was burned:fi~st ~er:6213 cycle~ his coxxespond~d:~
to an incxease ~f o~er 15~
~In ~IG. 3~he determin~d~:~thermal::str~eng~h~;were ~h~wn, a~d l~ aan be.3een~tha~:~he~ invent1ve mo~i~ied~alloy ~:;
1 has highe~ therm21 strengths value in the total tempera~ure tes~ing region.
FIG. 4 shows the achieved c~cle numbe~ during ~esting in ~ccordance wi~ FIG. ~b in d~pendence on ~he S ~pplied voltage. ~he modi~ied alloy ~howed at all load~ a significantly higher ser~rice li~e. At a ~ol~aye o~ 2 N/~m2 the 6-t~rne, ~ t}le ~oltage 3 N/rnm3 appro~:imately 5-~ime, and ~t ~he volt~ge ~ N/mm2 always 3.5-ti~e increa3e in t~e ser~ice liLe was achieved.
~l~o the ductili~y of a material duxin~ a long time use ~t high temperatures is an important ~truatural ~eatu~e.
The xeduc~ion of the duc~ility ~ n ~erriLia Fe-Cr-~l-al loys d~als wikh a 3trong gr~in grow~h at hig~ ~emE~eratuxes. In FIG. Sa the gxain size ~alues are px~sented ~or the probe a~ter ~ . 5 day~ stor~ge at ~50-1050C, in um ~upper curve ) .
More~ver, the ~ain si~e v~lues ~or the modifi~d al lo~ a~ter ~:
ato~:age time or 13 days a~ 950, 10~0 and 1150C are shown :
~ e~ curv~. -It can be 3een th~ the mQdified allo~ at the double s~oxa~e time has considerably more fine grain ~0 st~uc~ure than ~he co~parison alloy.
.
~ t~i~ there~ore not surpri~in~ that the bending numbers ~num~er o4 the k~ndings by 1~0 to ~reakag~ in accordance with ~IG. 5b is co~siderabl~ hi~her ~or ~he inven~ive modified alloy due o:its ~ine grain~tructure, ~5 than in the~so~parls~n alloy ~or:~e p~obe~ s ored during 13 3- ~
: ~-: ' ' ~:
, .
: ~
2 ~
o~ ~.5 d~y~ at temperatu~es 950, 1075 and 1175~C. l~h~
comparison shows that the mo~iied allo~ h~s a significantl~f hi~her ductili~y ~han the comparison allo~.
It will b~ unders~ood ~hat each o the elements des~ribed ~bo~e, or ~o or more ~oge~her, may also ~ind a use~ul applicatiorL in other types o con~txucti~ns dif~erin~
from the types desc~ibed above, While the iI~Vention has ~een il lus~ated ~nd desaribed as en~bodie~ in a heat de~crmable, ~rritio st~el al loy, it is rlot intended to k,e lirnited to the details s~own, since v~ious modiica~ions and a~ructural char~ges maY be made wi thout dapartin~ in any way from th~ spirit of l:he pre ent inv~ntion.
Withou~ furth~ anal~sis, :the foregoing will so fully reveaI the g~ist o~ t he present invention ~ha~ others can, by a~plyinq ou~rent ~owledge, readily adap~ it for va~ious applica~ic)ns without ~omitting ~atures ~hatj fro~ th2 st-andpoint o~ prlor a~t, ~alrly cons~itute ~ ess~ntial characte~igtics o the g~enerLC or speciic aspe~ts o~ this 2 0 inv~ntion .
What is claimed a3 new and~ dèslxed to be protected by Lette~s Paten~ ~s ~et ~forth in the ~appended cla~ims.
:
. ~
`: ~ :
-14- : :
~` . ' . '
Claims (8)
1. A heat-deformable, ferritic steel alloy, comprising:
20 up 25 % chromium 5 up to 8 % aluminum max. 0.01 % phosphorous max. 0.0l % rnagnes ium max. 0.5 % manganese max. 0.005 % sulfur rest iron including unavoidable impurities, also 0.03 up to 0.08 % ytrium 0.004 up to 0.008 % nitrogen 0.020 up to 0.040 % carbon and a substantially equal parts of 0.035 up to 0.07 % titanium 0.035 up to 0.07 % zirconium wherein the sum of the contents of titanium and zirconium in percentages is 1.75 - 3.5 times greater than the sum of the contents of C and N in percentages.
20 up 25 % chromium 5 up to 8 % aluminum max. 0.01 % phosphorous max. 0.0l % rnagnes ium max. 0.5 % manganese max. 0.005 % sulfur rest iron including unavoidable impurities, also 0.03 up to 0.08 % ytrium 0.004 up to 0.008 % nitrogen 0.020 up to 0.040 % carbon and a substantially equal parts of 0.035 up to 0.07 % titanium 0.035 up to 0.07 % zirconium wherein the sum of the contents of titanium and zirconium in percentages is 1.75 - 3.5 times greater than the sum of the contents of C and N in percentages.
2. An alloy as defined in claim 1, wherein the ratio of admixtures of titanium and zirconium lies in the region of 0.6 - 1.4.
3. An alloy as defined in claim 1, wherein the titanium and zirconium are replaced completely by hafnium and/or tantalum or vanadium.
4. An alloy as defined in claim 1, wherein the titanium and zirconium are partially replaced with hafnium and/of tantalum or vanadium.
5 . An alloy as defined in claim 3, wherein at least two of the elements Ti, Zr, Hf, Ta and V are replaced.
6. An alloy as defined in claim 4, wherein at least two of the elements Ti, Zr, Hf, Ta and V are replaced.
. .
. .
7, An alloy as defined in claim 3, wherein at least two of the elements Ti, Zr, Hf, Ta and V are replaced.
8 . An alloy as defined in claim 4, wherein at least two of the elements Ti, Zr, Hf, Ta and V are replaced.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| DEP3908526.0 | 1989-03-16 | ||
| DE3908526A DE3908526A1 (en) | 1989-03-16 | 1989-03-16 | FERRITIC STEEL ALLOY |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CA2012065A1 true CA2012065A1 (en) | 1990-09-16 |
Family
ID=6376432
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA002012065A Abandoned CA2012065A1 (en) | 1989-03-16 | 1990-03-13 | Heat-deformable, ferritic steel alloy |
Country Status (13)
| Country | Link |
|---|---|
| EP (1) | EP0387670B1 (en) |
| JP (1) | JPH03166341A (en) |
| KR (1) | KR960011803B1 (en) |
| AT (1) | ATE101659T1 (en) |
| AU (1) | AU621998B2 (en) |
| BR (1) | BR9001241A (en) |
| CA (1) | CA2012065A1 (en) |
| DD (1) | DD298950A5 (en) |
| DE (2) | DE3908526A1 (en) |
| ES (1) | ES2051399T3 (en) |
| IE (1) | IE63312B1 (en) |
| MX (1) | MX173057B (en) |
| ZA (1) | ZA901809B (en) |
Families Citing this family (14)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5340415A (en) * | 1992-06-01 | 1994-08-23 | Sumitomo Metal Industries, Ltd. | Ferritic stainless steel plates and foils and method for their production |
| JP3042788B2 (en) * | 1993-03-19 | 2000-05-22 | 日本冶金工業株式会社 | Ferritic stainless steel with excellent oxidation resistance |
| GB2285058B (en) * | 1993-12-24 | 1997-01-08 | Ceramaspeed Ltd | Radiant Electric Heater |
| FR2732360B1 (en) * | 1995-03-29 | 1998-03-20 | Ugine Savoie Sa | FERRITIC STAINLESS STEEL FOR USE, IN PARTICULAR FOR CATALYST SUPPORTS |
| DE19642497C1 (en) * | 1996-10-15 | 1997-07-24 | Krupp Vdm Gmbh | Iron@-chromium@-aluminium@ alloy foil production |
| DE19743720C1 (en) * | 1997-10-02 | 1998-12-24 | Krupp Vdm Gmbh | Cost effective production of iron alloy foil with high resistance to high temperature oxidation |
| DE19834552A1 (en) * | 1998-07-31 | 2000-02-03 | Krupp Vdm Gmbh | Oxidation resistant metal foil |
| DE19928842C2 (en) * | 1999-06-24 | 2001-07-12 | Krupp Vdm Gmbh | Ferritic alloy |
| DE10002933C1 (en) * | 2000-01-25 | 2001-07-05 | Krupp Vdm Gmbh | Iron-chromium-aluminum foil production, used e.g. as support material for exhaust gas treatment catalysts, comprises coating one or both sides of supporting strip with aluminum or aluminum alloys, and carrying out homogenizing treatment |
| DE10310865B3 (en) * | 2003-03-11 | 2004-05-27 | Thyssenkrupp Vdm Gmbh | Use of an iron-chromium-aluminum alloy containing additions of hafnium, silicon, yttrium, zirconium and cerium, lanthanum or neodymium for components in Diesel engines and two-stroke engines |
| WO2006083161A1 (en) * | 2004-11-23 | 2006-08-10 | Ferro Techniek Holding B.V. | Enamel composition, assembly and use thereof on a substrate surface |
| DE102007005154B4 (en) | 2007-01-29 | 2009-04-09 | Thyssenkrupp Vdm Gmbh | Use of an iron-chromium-aluminum alloy with a long service life and small changes in the heat resistance |
| DE102008018135B4 (en) | 2008-04-10 | 2011-05-19 | Thyssenkrupp Vdm Gmbh | Iron-chromium-aluminum alloy with high durability and small changes in heat resistance |
| CN104233083A (en) * | 2014-08-26 | 2014-12-24 | 盐城市鑫洋电热材料有限公司 | Precipitating strengthened electrothermal alloy and preparation method thereof |
Family Cites Families (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2191790A (en) * | 1938-05-07 | 1940-02-27 | Electro Metallurg Co | Steels and electrical resistance elements |
| JPS4945456B1 (en) * | 1969-06-25 | 1974-12-04 | ||
| GB2070642A (en) * | 1980-02-28 | 1981-09-09 | Firth Brown Ltd | Ferritic iron-aluminium- chromium alloys |
| GB2082631A (en) * | 1980-02-28 | 1982-03-10 | Firth Brown Ltd | Ferritic iron-aluminium-chromium alloys |
| JPS60262943A (en) * | 1984-06-08 | 1985-12-26 | Oosakafu | Iron-chromium-aluminum implant alloy for medical treatment |
| DE3706415A1 (en) * | 1987-02-27 | 1988-09-08 | Thyssen Edelstahlwerke Ag | SEMI-FINISHED FERRITIC STEEL PRODUCT AND ITS USE |
-
1989
- 1989-03-16 DE DE3908526A patent/DE3908526A1/en not_active Withdrawn
-
1990
- 1990-03-07 ES ES90104300T patent/ES2051399T3/en not_active Expired - Lifetime
- 1990-03-07 IE IE81990A patent/IE63312B1/en not_active IP Right Cessation
- 1990-03-07 DE DE90104300T patent/DE59004570D1/en not_active Expired - Lifetime
- 1990-03-07 EP EP90104300A patent/EP0387670B1/en not_active Expired - Lifetime
- 1990-03-07 AT AT90104300T patent/ATE101659T1/en not_active IP Right Cessation
- 1990-03-08 ZA ZA901809A patent/ZA901809B/en unknown
- 1990-03-13 AU AU51333/90A patent/AU621998B2/en not_active Expired
- 1990-03-13 CA CA002012065A patent/CA2012065A1/en not_active Abandoned
- 1990-03-14 DD DD90338707A patent/DD298950A5/en not_active IP Right Cessation
- 1990-03-15 BR BR909001241A patent/BR9001241A/en not_active IP Right Cessation
- 1990-03-15 JP JP2062840A patent/JPH03166341A/en active Granted
- 1990-03-15 KR KR1019900003495A patent/KR960011803B1/en not_active IP Right Cessation
- 1990-03-16 MX MX019940A patent/MX173057B/en unknown
Also Published As
| Publication number | Publication date |
|---|---|
| KR960011803B1 (en) | 1996-08-30 |
| IE63312B1 (en) | 1995-04-05 |
| MX173057B (en) | 1994-01-31 |
| ES2051399T3 (en) | 1994-06-16 |
| DE59004570D1 (en) | 1994-03-24 |
| KR900014614A (en) | 1990-10-24 |
| JPH03166341A (en) | 1991-07-18 |
| AU5133390A (en) | 1990-09-27 |
| EP0387670B1 (en) | 1994-02-16 |
| EP0387670A1 (en) | 1990-09-19 |
| AU621998B2 (en) | 1992-03-26 |
| DE3908526A1 (en) | 1990-09-20 |
| IE900819L (en) | 1990-09-16 |
| JPH0581657B2 (en) | 1993-11-15 |
| BR9001241A (en) | 1991-03-26 |
| DD298950A5 (en) | 1992-03-19 |
| ZA901809B (en) | 1991-04-24 |
| ATE101659T1 (en) | 1994-03-15 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CA2012065A1 (en) | Heat-deformable, ferritic steel alloy | |
| Pederson | Microstructure and phase transformation of Ti-6Al-4V | |
| CN110093522B (en) | Improvement of AlCoCrFeNi by magnetic field2.1Method for mechanical property of eutectic high-entropy alloy | |
| Van der Molen et al. | Control of γ′ particle size and volume fraction in the high temperature superalloy Udimet 700 | |
| US4080201A (en) | Nickel-base alloys | |
| US4288247A (en) | Nickel-base superalloys | |
| CN109972066B (en) | Method for improving AlCoCrCuFeNi high-entropy alloy force magnetic property by using magnetic field | |
| CN106636746B (en) | A kind of high-strength high-elongation ratio high-temperature titanium alloy and its preparation process | |
| Chastell et al. | The formation of the σ phase during long term high temperature creep of type 316 austenitic stainless steel | |
| EP0035369B1 (en) | Ferritic iron-aluminium-chromium alloys | |
| CN113832416A (en) | Method for regulating and controlling sigma phase of high-entropy alloy by using magnetic field | |
| US4006011A (en) | Controlled expansion alloy | |
| Shen et al. | Investigation of solidification modes of high Manganese steels | |
| Han et al. | Investigations on the solidification behavior of Al-Fe-Si alloy in an alternating magnetic field | |
| RU2747180C1 (en) | High-strength heat-resistant fine-grained alloy based on al-cu-mn-mg-sc-nb-hf system and its product | |
| Kawecki et al. | Research on mechanical and electrical properties of Cu-Ag alloys designed for the construction of high magnetic field generators | |
| CN110453129B (en) | Iron-nickel-chromium-based alloy, and preparation method and application thereof | |
| FAN et al. | Effect of thermal stabilization on microstructure and mechanical property of directionally solidified Ti–46Al–0.5 W–0.5 Si alloy | |
| Fernandes et al. | Evidence of the semi-solid formation in the medical grade TI6AL4V alloy using induction heating | |
| Schastlivaya et al. | Influence of the Composition of α-Titanium Alloys on Thermal Conductivity | |
| CN108277410B (en) | NbSi alloy with preferred orientation relation | |
| RU2706916C2 (en) | Blank for manufacturing elastic elements of a titanium-based alloy | |
| CN106048307B (en) | A kind of seven yuan are diphasic titanium alloy | |
| Udare et al. | Microstructural Evolution During Homogenization of Ni–Cu–Al–Ti Alloy | |
| SU1280038A1 (en) | Alloy with zero amplitude of neutron coherent scattering |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| EEER | Examination request | ||
| FZDE | Discontinued |