EP1215299B1 - Umwandlungskontrollierter Nitrid-ausscheidungshärtender Vergütungsstahl - Google Patents

Umwandlungskontrollierter Nitrid-ausscheidungshärtender Vergütungsstahl Download PDF

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Publication number
EP1215299B1
EP1215299B1 EP01128805A EP01128805A EP1215299B1 EP 1215299 B1 EP1215299 B1 EP 1215299B1 EP 01128805 A EP01128805 A EP 01128805A EP 01128805 A EP01128805 A EP 01128805A EP 1215299 B1 EP1215299 B1 EP 1215299B1
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EP
European Patent Office
Prior art keywords
weight
phase transformation
nitride precipitation
steel according
treatment steel
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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 - Lifetime
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EP01128805A
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German (de)
English (en)
French (fr)
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EP1215299A2 (de
EP1215299A3 (de
Inventor
Alkan Dr. Goecmen
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General Electric Technology GmbH
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Alstom Technology AG
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Publication of EP1215299A3 publication Critical patent/EP1215299A3/de
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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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/78—Combined heat-treatments not provided for above
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt

Definitions

  • the invention relates to a conversion-controlled nitride precipitation hardening agent Annealing steel with 15-18 wt .-% chromium, which through an optimal combination of strength, toughness and durability is characterized against stress corrosion cracking and which is therefore good in the chemical industry, traffic engineering, power plant technology, construction technology and at the Plastic processing can be used.
  • Conversion-controlled martensitic-hardenable steels are known in the art Technology, for example the alloy 17-5ph with 15.4% by weight Cr, 4.4% by weight Ni, 0.4% by weight of Mn, 0.25% by weight of Si, 3.3% by weight of Cu, 0.3% by weight Nb and 0.04% by weight C or the alloy 14-5 ph with 14% by weight Cr, 5% by weight Ni, 0.4% by weight Mn, 0.25 wt.% Si, 1.6 wt.% Cu, 0.25 wt.% Nb, 1.5 Mo and 0.05 wt.
  • the nickel and chromium contents are balanced so that no or only very little delta ferrite occurs during austenitization.
  • Conversion-controlled steels such as those in US-A-6 030 469, are strengthened by martensitic transformation and precipitation hardening. Martensite is produced by quenching treatment following austenitization, while precipitation hardening is achieved by heat treatment of the quenched martensite. Therefore, usually conversion controlled steels are first austenitized, quenched, and subsequently heat treated at medium temperatures. The respective microstructure formation is influenced by the effect of the alloying elements and the heat treatment parameters on the transformation temperatures M s , M f and A c1 .
  • M s is the temperature at which austenite to martensite transformation begins during quenching
  • M f is the temperature at which austenite to martensite transformation is terminated during quenching
  • a c1 is the temperature at which austenite formation occurs during the quench of heating up begins.
  • the M s temperature of the martensitic-hardenable steels is sufficiently high so that a majority of the austenite present during austenitization can be converted to martensite upon normal cooling to room temperature.
  • the M s temperature is further influenced by the grain size and the dissolved substitution elements, which enable precipitation hardening. The coarser the com and the higher the proportion of dissolved alloying elements, the lower the M s temperature.
  • the residual austenite remaining after complete austenitization and subsequent cooling treatment is convertible. If substitution elements are precipitated during a tempering treatment, the M s temperature of the retained austenite may again increase in such a way that it converts back into martensite during the subsequent cooling treatment.
  • the temper austenite must be distinguished from the tempering austenite, which remains after a partial austenitization, ie annealing in the ferrite-austenite two-phase region and subsequent cooling treatment.
  • Tempering austenite in contrast to retained austenite has a very favorable effect on the ductility (toughness) and the stress corrosion cracking resistance. It affects all the more favorable to these properties, the finer the previous (former) Austenitkom was.
  • the ductility is well enhanced by a two-fold austenitization, with the second austenitizing at lower austenitizing temperatures serving not only the grain refining (normalization) but also a limited precipitation of niobium carbides which, together with the grain refining, further increases the M s temperature.
  • Tempering austenite is formed during tempering at temperatures between 550 and 650 ° C, with a maximum content of tempering austenite being reached at temperatures around 600 ° C.
  • tempering austenite has a favorable effect on strength and Stress corrosion cracking resistance.
  • tempering austenite is specially at increased carbon contents, the formation of tempering austenite during a Tempering treatment in the range between 550 and 650 ° C with a sensitization of austenite.
  • the invention seeks to avoid these disadvantages. It's up to you based, a martensitic-hardenable steel, which improved Combination of strength, ductility and corrosion resistance, and a heat treatment process for such an alloy.
  • the core of the invention is a conversion-controlled nitride precipitation-hardening Heat-treated steel with the following composition (In% by weight): 15-18 Cr, maximum 0.5 Mn, 4-10 Ni, maximum 15 Co, maximum 4 W, maximum 4 Mo, 0.5-1 V, at least one of Nb, Ta, Hf and Zr in the Sum between 0.001-0.1, 0.001-0.05 Ti, maximum 0.5 Si, maximum 0.05 C, 0.13-0.25 N, a maximum of 4 Cu, balance iron and common impurities and the Provided that the weight ratio of vanadium to nitrogen V / N in Range is between 3.5 and 4.2.
  • the advantage of the invention is that by the choice of Alloying elements in addition to a high strength and ductility also a high Corrosion resistance is achieved.
  • the steel has 1-10% by weight of Co, 0.5-3, preferably 0.5-1.5% by weight of Cu; 15-17, preferably 15.5-16.5 wt% Cr; 0.5-0.7 Wt% V, 0.16-0.2 wt% N; 0.01-0.07 wt% Nb and a sum of Mo and W in the range 1-6, preferably 1-4.
  • Preferred contents of Mo are in the Range of 1.5-3 wt%, of Mn in the range of 0.02-0.4 wt%, of Si im Range of 0.02-0.25 wt%.
  • the C content is preferably 0.02 wt .-%.
  • the alloying elements have the following effects:
  • Chromium is the most important alloying element for corrosion resistance. One however, increasing proportion of alloy increases the retained austenite content. Above 17% chromium, a martensitic hardenability is no longer possible. Quality Alloys are expected to have chromium contents between 15 and 17%. One particularly preferred range is 15.5 to 16.5%.
  • Nickel is an austenite stabilizing element and is used to suppress delta ferrite. Within the scope of the desired alloy design at least 4% are necessary for this purpose. Increasing levels, however, lower the M s temperature and increase the retained austenite content. Above 10% nickel, a martensitic through-hardenability in the presence of about 15% chromium is no longer possible.
  • Cobalt is an austenite stabilizing element and is also used to suppress delta ferrite. Unlike nickel, however, it lowers the M s temperature far less so that martensitic-curable alloys with cobalt contents up to 15% can be designed. Further, cobalt enhances precipitation hardenability by molybdenum and tungsten. Considering the high cobalt price and the achievable improvements, a preferred range is 1 to 7% cobalt.
  • Both elements contribute to strength through solid-solution hardening. At elevated levels, they can also significantly increase firmness through precipitation hardening. However, both elements also lower the M s temperature and thus increase the residual austenite content. Therefore, the preferred amount of molybdenum and tungsten is limited to a total of 6%. It is also known that molybdenum improves corrosion resistance. Therefore, molybdenum is preferred over tungsten.
  • the preferred range of Mo is 1 to 4%. A particularly preferred range is 1.5 to 3%.
  • V to N A preferred ratio of V to N is 3.5 to 4.2.
  • the preferred content of nitrogen is in the range between 0.16 and 0.20 % and that of vanadium in the range between 0.5 and 0.7%.
  • titanium leads to the formation of titanium nitrides. This phase can significantly contribute to grain refining and grain size limitation.
  • the addition of more than 0.05% titanium leads to the formation of less effective, coarse Titanium nitrides, which is why the proportion of titanium should be limited to 0.05%.
  • Manganese is an austenite stabilizing element. However, its effect of suppressing delta ferrite is not as strong as that of nickel and cobalt. On the other hand, it greatly lowers the M s temperature. This combination of properties is very unfavorable in the context of the desired alloy design. Therefore, the weight content of manganese should not exceed 0.5%.
  • Silicon should be used exclusively for deoxidation purposes. Too high Contents, however, lower toughness. Therefore, the weight percentage of Silicon be limited to 0.5%.
  • Carbon is an element effective in suppressing detta ferrite. On the other hand, this element leads to an additional reduction of the M s temperature and must therefore be limited to 0.05%. In addition, during the tempering treatment, carbon promotes grain boundary precipitation of chromium carbides and thus deteriorates corrosion resistance (sensitization). The carbon should therefore preferably be limited to 0.03%.
  • Fig. 1 shows schematically the structure of an inventive alloy. It is martensitic and is divided into former Austenitgromer 1, which in Martensite crystals (blocks) 2 are decomposed, which in turn are divided into a set of columnar Subkömem (slats) 3 are decomposed.
  • Vanadium nitrides 5 or vanadium / niobium nitrides 4 are in this structure embedded. These nitrides either have high austenitizing temperatures survived (primary nitrides 4) or were in subsequent Heat treatment stages formed (secondary nitrides 5). Secondary nitrides 5 can during a Reaustenitmaschine at lower temperatures as well during a tempering treatment of martenitis 2 are formed.
  • Austenitgromer 6 are also embedded.
  • This austenite 6 is to be understood as tempering austenite, since it is a final austerity Annealing is generated and after cooling to room temperature remains.
  • the primary nitrides 4 are slightly coarser than the secondary nitrides 5, but both Nitride types 4 and 5 are very evenly distributed. Through this regularity an optimized curing effect is achieved. This happens both over Grain refining as well as particle hardening. By the regularity and due to the low coarsening tendency of the primary vanadium / niobium mixed nitrides 4, resistance to massive grain coarsening is up Temperatures of 1180 ° C ensured.
  • Nitrides which are dissolved at austenitisation at 1180 ° C, can be re-excreted to a large extent at a Reaustenitmaschine between 730 and 850 ° C. These nitrides 5 remain sufficiently fine that they contribute to the overall realized strength by particle curing. It is essential, however, that a grain refinement is associated with the reaustenitization, which is effectively supported by the presence of the primary nitrides 4 as well as the newly forming vanadium nitrides 5. Grain refining and reprecipitation of nitrides 5 together allow a very effective increase in M s temperature.
  • Tempering austenite 6 develops at temperatures between 550 and 650 ° C. Above a temperature of 600 ° C, vanadium nitrides 5 can easily be in the martensitic matrix 2 are excreted and provide a significant Strength contribution. Of importance is that the emerging temper austenite 6 in its growth is strongly affected by the presence of nitrides 4, 5. So if it is possible to produce austenite 6 in a high germ density, it can within martensite 2 and under the action of the present nitrides 4, 5 evenly and finely distributed. An increased germ density can by a fine martensite 2 can be ensured.
  • the precipitation hardening can be further increased by copper.
  • a further precipitation hardening is due to the addition of molybdenum and / or Tungsten in combination with nickel and cobalt possible.
  • the addition of molybdenum can further improve the corrosion resistance.
  • FIGS. 2 to 5 show strength and hardness values of the alloys AP39, AP40 and AP41 according to the invention in comparison to the reference alloys 14-5ph and 17-4ph.
  • Fig. 2 shows the tempering curves of the inventive alloys AP39, AP40 and AP41, which were solution annealed at 1180 ° C / 2h compared to commercial alloy of the type 17-4ph, which solution-annealed at 1050 ° C / 2 h has been. All test samples with a cross section of 30 mm were cooled in air. The start time was 2 hours each. It became the Vickers Hardness HV 10 of the examined samples as a function of the tempering temperature T applied. It can be clearly seen that at tempering temperatures above of 600 ° C in the inventive alloys much higher Hardness values can be achieved than in the comparison alloy.
  • Figures 3 to 5 show strength values of the inventive alloys AP39 (Fig. 3), AP40 (Fig. 4) and AP41 (Fig.5) after a solution annealing at 1180 ° C, an intermediate annealing at 640 ° C, 730 ° C or 780 ° C, as well as a final tempering treatment at 600 ° C.
  • the strengths (yield strength Rp 0.2 and tensile strength R m ) are compared with typical values of the alloy 14-5ph known in the prior art in the heat treatment state LZA450, LZA550 and LZA4620.
  • the open symbols refer to the yield strength, the closed symbols to the tensile strength.
  • All three alloys according to the invention have the final one Tempering at 600 ° C tensile strength values close or clear above the upper scattering end of the type 14-5ph steel.
  • the alloys A39 and A41 show after the final Tempering at 600 ° C yield strength values, which are close or clear above the upper scattering end of the type 14-5ph steel.
  • tempering temperatures of about 550 ° C must be applied. This means that even in the one Temperature range in which the tempering austenite preferably forms, still high Strength values can be achieved.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
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  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
EP01128805A 2000-12-18 2001-12-04 Umwandlungskontrollierter Nitrid-ausscheidungshärtender Vergütungsstahl Expired - Lifetime EP1215299B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE10063117A DE10063117A1 (de) 2000-12-18 2000-12-18 Umwandlungskontrollierter Nitrid-ausscheidungshärtender Vergütungsstahl
DE10063117 2000-12-18

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EP1215299A2 EP1215299A2 (de) 2002-06-19
EP1215299A3 EP1215299A3 (de) 2003-12-10
EP1215299B1 true EP1215299B1 (de) 2005-03-09

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US (1) US6592685B2 (zh)
EP (1) EP1215299B1 (zh)
CN (1) CN1252305C (zh)
DE (2) DE10063117A1 (zh)

Families Citing this family (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20070261768A1 (en) * 2006-05-10 2007-11-15 Reynolds Harris A Jr Method for designing corrosion resistant alloy tubular strings
US10351922B2 (en) 2008-04-11 2019-07-16 Questek Innovations Llc Surface hardenable stainless steels
EP2265739B1 (en) 2008-04-11 2019-06-12 Questek Innovations LLC Martensitic stainless steel strengthened by copper-nucleated nitride precipitates
CN101693976B (zh) * 2009-10-14 2011-06-15 马鞍山钢铁股份有限公司 转炉炼钢的钒氮微合金化方法
CN102001442B (zh) * 2010-11-16 2013-09-18 宝鼎重工股份有限公司 一种铸造成型的桨叶导向架及铸造成型方法
CN102001441B (zh) * 2010-11-16 2013-04-10 宝鼎重工股份有限公司 一种铸造成型的桨叶导向架及铸造成型方法
UA111115C2 (uk) 2012-04-02 2016-03-25 Ейкей Стіл Пропертіс, Інк. Рентабельна феритна нержавіюча сталь
CN103736945A (zh) * 2013-12-05 2014-04-23 天水星火机床有限责任公司 一种减少铁水浇注件裂纹的方法
WO2015163509A1 (en) * 2014-04-25 2015-10-29 Songwon Industrial Co., Ltd. Hydrogel comminuting device comprising rotating steel component in the production of water-absorbent polymer particles

Family Cites Families (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE891399C (de) * 1940-06-20 1953-09-28 Eisen & Stahlind Ag Austenitische Stahllegierungen fuer Gegenstaende, die bei ihrer Herstellung oder im Betrieb einer Erwaermung ausgesetzt werden
US5415706A (en) * 1993-05-28 1995-05-16 Abb Management Ag Heat- and creep-resistant steel having a martensitic microstructure produced by a heat-treatment process
RU2071989C1 (ru) * 1993-07-22 1997-01-20 Московский институт стали и сплавов Сталь (ее варианты)
US5650024A (en) * 1993-12-28 1997-07-22 Nippon Steel Corporation Martensitic heat-resisting steel excellent in HAZ-softening resistance and process for producing the same
JP3388998B2 (ja) * 1995-12-20 2003-03-24 新日本製鐵株式会社 溶接性に優れた高強度オーステナイト系耐熱鋼
DE19614407A1 (de) * 1996-04-12 1997-10-16 Abb Research Ltd Martensitisch-austenitischer Stahl
DE19712020A1 (de) * 1997-03-21 1998-09-24 Abb Research Ltd Vollmartensitische Stahllegierung
DE19740908C1 (de) * 1997-09-17 1999-08-05 Vacuumschmelze Gmbh Anzeigeelement für die Verwendung in einem magnetischen Diebstahlsicherungssystem und Verfahren zur Herstellung eines Aktivierungsstreifens hierfür
DE10025808A1 (de) * 2000-05-24 2001-11-29 Alstom Power Nv Martensitisch-härtbarer Vergütungsstahl mit verbesserter Warmfestigkeit und Duktilität

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Publication number Publication date
US6592685B2 (en) 2003-07-15
CN1368560A (zh) 2002-09-11
DE10063117A1 (de) 2003-06-18
CN1252305C (zh) 2006-04-19
US20020139449A1 (en) 2002-10-03
EP1215299A2 (de) 2002-06-19
EP1215299A3 (de) 2003-12-10
DE50105523D1 (de) 2005-04-14

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