EP0225263B1 - Tôle ou bande en acier ferritique inoxydable, en particulier pour systèmes d'échappement - Google Patents

Tôle ou bande en acier ferritique inoxydable, en particulier pour systèmes d'échappement Download PDF

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Publication number
EP0225263B1
EP0225263B1 EP86420267A EP86420267A EP0225263B1 EP 0225263 B1 EP0225263 B1 EP 0225263B1 EP 86420267 A EP86420267 A EP 86420267A EP 86420267 A EP86420267 A EP 86420267A EP 0225263 B1 EP0225263 B1 EP 0225263B1
Authority
EP
European Patent Office
Prior art keywords
strip
sheet
resistance
oxidation
test
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.)
Expired
Application number
EP86420267A
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German (de)
English (en)
French (fr)
Other versions
EP0225263A1 (fr
Inventor
Pascal Gressin
Philippe Maitrepierre
Jean Decroix
Pierre Pedarre
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Ugine Aciers de Chatillon et Guegnon
Original Assignee
Ugine Aciers de Chatillon et Guegnon
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Ugine Aciers de Chatillon et Guegnon filed Critical Ugine Aciers de Chatillon et Guegnon
Priority to AT86420267T priority Critical patent/ATE42770T1/de
Publication of EP0225263A1 publication Critical patent/EP0225263A1/fr
Application granted granted Critical
Publication of EP0225263B1 publication Critical patent/EP0225263B1/fr
Expired legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • 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

Definitions

  • the invention relates to the field of rolled products of stainless ferritic steel, and more particularly that of exhaust systems.
  • the Applicant has tried to improve the properties compromises obtained with sheets or strips of shades already known and more particularly with stainless ferritic grades stabilized with Nb and / or Zr, and this especially with regard to the creep resistance and to hot oxidation.
  • Ferritic stainless grades are superior to austenitic grades because of their coefficient of thermal expansion.
  • Patent application FR-A-2 463194 relates to ferritic steels with 1 to 20% Cr and Ti, Nb with 0.5 to 2% AI, in which a minimum AI content of 0.5% and preferably 0.75% is required to provide resistance to oxidation at elevated temperatures. Above 2%, AI has a detrimental effect on the weldability.
  • a ferritic stainless steel contains 0.08 to 0.5% AI and one or more of the elements B (2-50 ppm), Ti (0.005-0.4%), Nb (0.005-0.4%), V (0.005-0.4%) and Zr (0.005-0.4%), and AI results in structural changes at the various stages of sheet metal transformation with an increase in “ridging resistance” (resistance to the phenomenon of stringing or crumpling).
  • Zrest consumed by stabilization that is to say by trapping C and N in the form of nitrides and carbides, up to approximately 7 (C + N)%.
  • the free Zr is therefore limited to 0.2%, which makes it possible to avoid the drawbacks linked to the formation of eutectic compounds containing Fe 3 Zr in the case where there is more than 0.25% of free Zr, these compounds resulting in a degradation of the mechanical characteristics, in particular of the ductility and of the creep resistance, and a reduction in the corrosion resistance, as indicated essentially by document US-A-4010049.
  • the free Zr has no significant direct influence on the resistance to oxidation.
  • the free or non-combined Nb is between 0.25 and 0.55%.
  • the Nbtotal includes in addition to the free Nb an addition of 7 (C + N) -Zr, to compensate for the lack of stabilization by insufficient Zr, in the case where Zr is between 7 (C + N) - 0.1 and 7 (C + N).
  • the total content of AI assayed corresponds essentially to AI in solid solution.
  • Zr has more affinity than AI for oxygen and there is little residual oxygen in the metal, so that there can be only very little AI in the form of alumina.
  • the affinities of Zr and Nb for nitrogen and the greater affinity of AI for oxygen than for nitrogen means that aluminum nitride AIN does not form.
  • the result confirmed qualitatively by micrographic examinations, is that AI is in solid solution with the exception of a content at most equal to 0.003% and corresponding essentially to alumina.
  • 0.020 to 0.080% AI a surprising improvement in resistance to hot oxidation is obtained, linked to the role of aluminum in solid solution, whether it is continuous oxidation.
  • the AI content is limited to 0.080% so as to avoid, as has been the experience with 17% Cr stainless steels (type AISI 430), dross on the weld beads causing irregular oxidation and cracking conformation, therefore faster corrosion.
  • This dross effect is significant at the 0.1% AI level; but if one also wants to avoid or limit the inclusions of alumina linked to the presence of too much aluminum, these inclusions being sites of initiation of stings following the projections of salt water coming from salting or desalination of roads during winter, it is advisable to remain below 0.05% of AI as it is done in the preferential composition indicated below.
  • AI 0.020 to 0.045 and more preferably 0.025 to 0.040.
  • the sheet or strip according to the invention is in the annealed and optionally erected state, this annealed state typically corresponding to a treatment at 1000 ⁇ 10 ° C for 0.5 to 5 min.
  • the invention also relates to the method of manufacturing a sheet or strip of ferritic stainless steel, in which, as is known, the hot rolled strip is annealed with a thickness of between 2.5 and 5 mm between 800 and 1000 ° C. under slightly oxidizing conditions, then it is shot and pickled, then it is cold rolled to the delivery thickness typically between 0.6 and 3 mm, with or without annealing and intermediate pickling, and it is annealed at the end of the parade, then it is subjected to a finishing pass or so-called "skin-pass" hardening producing an elongation of less than 1%, with possibly a final stripping.
  • the hot rolled strip is annealed with a thickness of between 2.5 and 5 mm between 800 and 1000 ° C. under slightly oxidizing conditions, then it is shot and pickled, then it is cold rolled to the delivery thickness typically between 0.6 and 3 mm, with or without annealing and intermediate pickling, and it is annealed at the end of the parade, then
  • This process differs from the prior art in that the sheet or strip has the composition of the invention and in that the annealing, making it possible to obtain good hot creep results, is carried out between 980 and 1020 ° C. , and preferably between 990 and 1010 ° C for 0.5 to 5 min, or at a temperature and for a time giving an equivalent metallurgical state.
  • This final annealing is typically carried out following a rolling producing an elongation of at least 100% from the previous annealing.
  • Rectangular test specimens of 310 x 25 mm were cut from the sheets, and bent at 90 ° to 25 mm from one end. Then they were laid flat each on 2 supports of internal distance 254 mm and external distance 264 mm and they were subjected to continuous SAGTEST tests of creep under their own weight during 100 h at 850 ° C.
  • the sheets according to the invention with an uncombined Nb content of between 0.25 and 0.55%, and preferably with the intervals specified above, are thus indicated by their level of resistance to hot creep.
  • creep tests in tension at 800 ° C confirmed the SAGTEST tests.
  • the welds of the sheets according to the invention all exhibit very good ductility, unlike sheets with Nb + AI, and this even in the case of casting No. 445 where the Zr content is slightly less than 7 (C + N) .
  • the samples used come from 3 flows of 25 kg transformed according to the process indicated in connection with the test series N ° 1, the cold rolling being stopped at the thickness 1.5 mm and being followed by annealing under vacuum. from 1 h at 830 ° C.
  • the analyzes of the 3 castings, at 0.4% Nb and with increasing AI content, are shown in Table 7.
  • the samples are 20 x 30 mm plates cut out with a punch. in the annealed 1.5 mm sheets, then electrolytically polished in an aceto-perchloric bath (88-12) at room temperature for 5 min, then weighed in mg.
  • Each oxidation test relates to 3 test pieces of the same type, with an additional test piece for metallographic examinations.
  • the hot air oxidation tests have a unit duration of 50 h, the air renewal is ensured by "chimney effect" by means of a ⁇ 6 mm hole made in the lower part of the oven.
  • the oxides formed are removed by electrolytic pickling in a neutral medium, and it is the weight loss of the samples per unit area (in g / m 2 ) which makes it possible to assess "a contrario" the resistance to hot oxidation.
  • the results on the 3 test pieces of each test are well grouped in the case of continuous oxidation, and we have therefore given in this case only one result, average of the 3 individual results.
  • the AI contents are plotted on the graph in FIG. 4.
  • test pieces prepared as described above are subjected to cycles each comprising: rapid heating, holding for 10 min at the test temperature, then air cooling and maintaining at room temperature or close to total duration 10 min.
  • the duration of a test is 100 h during which 300 cycles are carried out giving an overall maintenance at the test temperature of 50 h.
  • test pieces from casting with Nb + Al No 101 and casting according to the invention N os 201 and 202, the analyzes of which appear in table 7.
  • the tests relate to both full-sheet test pieces and test pieces containing welds, the latter being carried out as indicated with regard to the series of tests No. 2, and the right side of these welds then occupying% of the width of the test pieces.
  • the sheets of the invention are therefore distinguished from sheets of Nb without Zr in that their welds without filler metal have better resistance to alternating or cyclic oxidation in this temperature range (850 to 950 ° C) important for exhaust manifolds.
  • the strips or sheets of the invention are used for any application in which an economic compromise of ductility (sheet metal and welds), heat resistance (creep, continuous or cyclic air oxidation) and resistance to corrosion.
  • Application to exhaust systems is particularly typical.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Organic Chemistry (AREA)
  • Metallurgy (AREA)
  • Mechanical Engineering (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Catalysts (AREA)
  • Exhaust Gas Treatment By Means Of Catalyst (AREA)
  • Treating Waste Gases (AREA)
  • Soft Magnetic Materials (AREA)
  • Heat Treatment Of Steel (AREA)
  • Exhaust Silencers (AREA)
  • Woven Fabrics (AREA)
EP86420267A 1985-11-05 1986-10-29 Tôle ou bande en acier ferritique inoxydable, en particulier pour systèmes d'échappement Expired EP0225263B1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
AT86420267T ATE42770T1 (de) 1985-11-05 1986-10-29 Blech oder band aus ferritischem rostfreien stahl, insbesondere fuer auspuffsysteme.

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR8516781A FR2589482B1 (fr) 1985-11-05 1985-11-05 Tole ou bande en acier ferritique inoxydable, en particulier pour systemes d'echappement
FR8516781 1985-11-05

Publications (2)

Publication Number Publication Date
EP0225263A1 EP0225263A1 (fr) 1987-06-10
EP0225263B1 true EP0225263B1 (fr) 1989-05-03

Family

ID=9324764

Family Applications (1)

Application Number Title Priority Date Filing Date
EP86420267A Expired EP0225263B1 (fr) 1985-11-05 1986-10-29 Tôle ou bande en acier ferritique inoxydable, en particulier pour systèmes d'échappement

Country Status (14)

Country Link
US (1) US4726853A (no)
EP (1) EP0225263B1 (no)
JP (1) JPS62112757A (no)
AT (1) ATE42770T1 (no)
AU (1) AU585083B2 (no)
BR (1) BR8605431A (no)
CA (1) CA1285791C (no)
DE (1) DE3663150D1 (no)
DK (1) DK518886A (no)
ES (1) ES2008092B3 (no)
FR (1) FR2589482B1 (no)
NO (1) NO167307C (no)
PT (1) PT83679B (no)
ZA (1) ZA868359B (no)

Families Citing this family (26)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE3706415A1 (de) * 1987-02-27 1988-09-08 Thyssen Edelstahlwerke Ag Halbfertigerzeugnis aus ferritischem stahl und seine verwendung
US4834808A (en) * 1987-09-08 1989-05-30 Allegheny Ludlum Corporation Producing a weldable, ferritic stainless steel strip
DE68919606T2 (de) * 1988-09-05 1995-04-06 Hitachi Metals Ltd Hitzebeständige Gussstähle.
US4942922A (en) * 1988-10-18 1990-07-24 Crucible Materials Corporation Welded corrosion-resistant ferritic stainless steel tubing having high resistance to hydrogen embrittlement and a cathodically protected heat exchanger containing the same
EP0387901B1 (en) * 1989-03-17 1994-11-02 Kawasaki Steel Corporation Stainless steel sheet for exterior building constituent and method of making the same
US5288343A (en) * 1989-03-17 1994-02-22 Kawasaki Steel Corporation Stainless steel sheet for exterior building constituent
DE3911104C1 (no) * 1989-04-06 1990-11-29 Krupp Stahl Ag, 4630 Bochum, De
US5110544A (en) * 1989-11-29 1992-05-05 Nippon Steel Corporation Stainless steel exhibiting excellent anticorrosion property for use in engine exhaust systems
JPH0747799B2 (ja) * 1989-11-29 1995-05-24 新日本製鐵株式会社 耐食性の優れたエンジン排ガス系材料用ステンレス鋼
US5302214A (en) * 1990-03-24 1994-04-12 Nisshin Steel Co., Ltd. Heat resisting ferritic stainless steel excellent in low temperature toughness, weldability and heat resistance
JP2696584B2 (ja) * 1990-03-24 1998-01-14 日新製鋼株式会社 低温靭性，溶接性および耐熱性に優れたフエライト系耐熱用ステンレス鋼
JP2562740B2 (ja) * 1990-10-15 1996-12-11 日新製鋼株式会社 耐粒界腐食性，造管性および高温強度に優れたフエライト系ステンレス鋼
WO1993021356A1 (en) * 1992-04-09 1993-10-28 Nippon Steel Corporation Ferritic stainless steel with excellent high-temperature salt injury resistance and high-temperature strength
JPH06220545A (ja) * 1993-01-28 1994-08-09 Nippon Steel Corp 靱性の優れたＣｒ系ステンレス鋼薄帯の製造方法
ES2184767T3 (es) * 1993-04-27 2003-04-16 Nisshin Steel Co Ltd Acero inoxidable ferritico excelente por su resistencia a la oxidacion a alta temperatura y a la adherencia de la capa de oxido.
DE69500714T2 (de) * 1994-04-21 1998-03-26 Kawasaki Steel Co Heissgewalzter ferritischer Stahl für eine Kraftfahrzeug-Abgasanlage
EP0786140B1 (en) * 1994-10-11 2000-06-14 Crs Holdings, Inc. Corrosion-resistant magnetic material
SE504295C2 (sv) * 1995-04-21 1996-12-23 Avesta Sheffield Ab Förfarande för kallvalsning-glödgning-kallsträckning av ett varmvalsat rostfritt stålband
FR2798394B1 (fr) * 1999-09-09 2001-10-26 Ugine Sa Acier ferritique a 14% de chrome stabilise au niobium et son utilisation dans le domaine de l'automobile
ES2230227T3 (es) * 2000-12-25 2005-05-01 Nisshin Steel Co., Ltd. Lamina de acero inoxidable ferritico con buena trabajabilidad y metodo para su fabricacion.
DE60224249T3 (de) 2001-09-27 2012-10-18 Hitachi Metals, Ltd. Stahl für Festoxid-Brennstoffzellenseparatoren
WO2005014873A1 (ja) * 2003-08-06 2005-02-17 Nisshin Steel Co., Ltd. ステンレス鋼の加工硬化材
KR20060089136A (ko) * 2005-02-03 2006-08-08 닛신 세이코 가부시키가이샤 Ｃｐｕ 소켓 프레임용 또는 ｃｐｕ 고정 커버용 고강성스테인레스강판
EP1818421A1 (fr) * 2006-02-08 2007-08-15 UGINE & ALZ FRANCE Acier inoxydable ferritique dit à 19% de chrome stabilisé au niobium
SI3670692T1 (sl) 2018-12-21 2022-11-30 Outokumpu Oyj, Feritno nerjavno jeklo
CN116145030B (zh) * 2022-12-23 2023-12-15 鞍钢股份有限公司 三代核电站关键设备支撑用铁素体不锈钢钢板及制造方法

Family Cites Families (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4010049A (en) * 1975-10-06 1977-03-01 Jones & Laughlin Steel Corporation Columbium-stabilized high chromium ferritic stainless steels containing zirconium
DE2701329C2 (de) * 1977-01-14 1983-03-24 Thyssen Edelstahlwerke AG, 4000 Düsseldorf Korrosionsbeständiger ferritischer Chrom-Molybdän-Nickelstahl
US4261739A (en) * 1979-08-06 1981-04-14 Armco Inc. Ferritic steel alloy with improved high temperature properties

Also Published As

Publication number Publication date
ES2008092B3 (es) 1989-07-16
NO167307C (no) 1991-10-23
ATE42770T1 (de) 1989-05-15
CA1285791C (fr) 1991-07-09
FR2589482B1 (fr) 1987-11-27
NO864394D0 (no) 1986-11-04
PT83679B (pt) 1989-06-30
FR2589482A1 (fr) 1987-05-07
DE3663150D1 (en) 1989-06-08
ZA868359B (en) 1987-06-24
NO864394L (no) 1987-05-06
EP0225263A1 (fr) 1987-06-10
JPS62112757A (ja) 1987-05-23
DK518886D0 (da) 1986-10-30
PT83679A (fr) 1986-12-01
BR8605431A (pt) 1987-08-11
NO167307B (no) 1991-07-15
US4726853A (en) 1988-02-23
AU6480286A (en) 1987-05-07
AU585083B2 (en) 1989-06-08
DK518886A (da) 1987-05-06

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