EP1158067A1 - Acier de traitement thermique durcissable martensitique à résistance thermique ameliorée et à ductilité ameliorée - Google Patents

Acier de traitement thermique durcissable martensitique à résistance thermique ameliorée et à ductilité ameliorée Download PDF

Info

Publication number
EP1158067A1
EP1158067A1 EP01108810A EP01108810A EP1158067A1 EP 1158067 A1 EP1158067 A1 EP 1158067A1 EP 01108810 A EP01108810 A EP 01108810A EP 01108810 A EP01108810 A EP 01108810A EP 1158067 A1 EP1158067 A1 EP 1158067A1
Authority
EP
European Patent Office
Prior art keywords
martensitic
ductility
nickel
steel according
hardenable
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.)
Granted
Application number
EP01108810A
Other languages
German (de)
English (en)
Other versions
EP1158067B1 (fr
Inventor
Alkan Dr. Goecmen
Peter Dr. Ernst
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.)
General Electric Technology GmbH
Original Assignee
Alstom Schweiz AG
Alstom Power NV
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 Alstom Schweiz AG, Alstom Power NV filed Critical Alstom Schweiz AG
Publication of EP1158067A1 publication Critical patent/EP1158067A1/fr
Application granted granted Critical
Publication of EP1158067B1 publication Critical patent/EP1158067B1/fr
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

Images

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
    • C22C38/40—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
    • 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
    • C22C38/44—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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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
    • 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
    • C21D6/02—Hardening by precipitation

Definitions

  • the invention relates to martensitic hardenable steels with elevated Nitrogen content. It affects both the choice and the quantitative proportion Tuning special alloy elements, which the setting of a exceptionally good combination of heat resistance and ductility enable, as well as a method for heat treatment of the alloy according to the invention.
  • Martensitic hardenable steels based on 9-12% chromium are widespread Power plant engineering materials. It is known that the addition of chromium in the above range not only good resistance to atmospheric Corrosion, but also the complete hardenability of thick-walled Forgings made possible, such as as monoblock rotors or as Rotor disks are used in gas and steam turbines. Proven Alloys of this type usually contain about 0.08 to 0.2% carbon, which in solution is the setting of a hard martensitic structure enables.
  • a good combination of heat resistance and ductility martensitic steels is made possible by a tempering treatment in which through the excretion of carbon in the form of carbides simultaneous recovery of the dislocation substructure a particle stabilized Sub-grain structure forms.
  • the starting behavior and the resulting Properties can be effective through the choice and the proportion Matching special carbide formers such as Mo, W, V, Nb and Ta to be influenced.
  • Strengths over 850 MPa of 9-12% chrome steels can be set by lowering the tempering temperature, typically in the range 600 to 650 ° C, is held.
  • the use of low tempering temperatures leads to high ones Transition temperatures from brittle to ductile (above 0 ° C), with which the material exhibits brittle fracture behavior at room temperature. Clear Improved ductility can be achieved if the tempered strength is lowered below 700 MPa. This is done by raising the Tempering temperature reached over 700 ° C.
  • the application increased Tempering temperatures has the advantage that the set structural states are stable over long periods at elevated temperatures.
  • a typical one Representative who is wide in steam power plants, especially as rotor steel German steel known as DIN has been used X20CrMoV12.1.
  • the ductility is at a strength level of 850 MPa can be significantly improved by alloying with nickel. That's about it known that by alloying about 2 to 3% nickel even after a Tempering treatment at temperatures from 600 to 650 ° C Transition temperature from brittle to ductile state is still below 0 ° C, which results in a significantly improved combination of strength and Ductility. Such alloys are therefore widely used there Use where significantly higher demands on both strength and Ductility, typically used as disc materials for Gas turbine rotors. A typical representative of such alloys, which in the Gas turbine technology, especially as a material for rotor disks wide German steel known as DIN has been used X12CrNiMo12.
  • European patent application EP 0 931 845 A1 describes one in the Constitution similar to the German steel X12CrNiMo12, containing 12% nickel Chrome steel, in which the element molybdenum compared to the known steel X12 CrNiMo12 reduced, however an increased content of tungsten was added.
  • EP 0 866 145 A2 describes a new class of martensitic Chromium steels with nitrogen contents in the range between 0.12 to 0.25% described.
  • the entire structure is determined by Formation of special nitrides, in particular controlled by vanadium nitrides, which through the forging treatment, through the austenitization, through a controlled cooling treatment or through a tempering treatment in various Way can be distributed.
  • the nitride is achieved by setting a high ductility in this Patent application through the distribution and morphology of nitrides, especially but by limiting the coarsening of the grain during forging and sought during solution heat treatment.
  • the invention has for its object a martensitic curable To create tempered steel with high ductility, which is compared to the known prior art, in particular the steel X12CrNiMo12, by a characterized by increased heat resistance at temperatures from 300 to 600 ° C. It should on the one hand a suitable steel composition and on the other hand a Heat treatment process for materials of this composition be specified, which is the formation of a ductile and simultaneous heat-resistant martensitic tempering structure.
  • the core of the invention is a martensitic hardenable tempering steel with the following Composition (data in% by weight): 9 to 13% Cr, 0.001 to 0.25% Mn, 2 up to 7% Ni, 0.001 to 8% Co, at least one of W and Mo in total between 0.5 and 4%, 0.5 to 0.8% V, at least one of Nb, Ta, Zr and Hf in the sum between 0.001 to 0.1%, 0.001 to 0.05% Ti, 0.001 to 0.15% Si, 0.01 to 0.1% C, 0.12 to 0.18% N, maximum 0.025% P, maximum 0.015% S, maximum 0.01% Al, maximum 0.0012% Sb, maximum 0.007% Sn, maximum 0.012 % As, remainder iron and usual impurities, and the proviso that the Weight ratio of vanadium to nitrogen V / N in the range between 3.5 and 4.2 lies.
  • the advantage of the invention is that in the alloy mentioned Occasional structure is set, which is characterized by a tough basic matrix and the presence of nitrides that provide heat resistance.
  • the toughness of the Basic matrix is preferred by the presence of substitution elements by nickel and secondarily by cobalt.
  • the levels of this Substitution elements are designed to optimally unfold both martensite hardening and particle hardening using special nitrides, preferably vanadium nitrides, for setting the highest heat resistance enable.
  • One of the known martensitic-hardenable 9-12% chrome steels can be used good combination of heat resistance and ductility through a Stop compensation treatment, which is an austenitization treatment, a Quenching treatment and tempering treatment included.
  • the attainable Strength is largely determined by the basic hardness of the quenched Martensite and the potential particle hardening effect of Elimination phases that are formed during the tempering treatment limited.
  • An increase in strength over the basic hardness of the quenched Martensits is also through an occasion treatment in the so-called Secondary curing area possible. This is for those in power plant technology well-known 12% chrome steels in the temperature range between 450 and about 530 ° C.
  • both hardening mechanisms lower both the martensitic Hardening as well as precipitation hardening, ductility. More characteristic A ductility minimum is thus achieved in the area of secondary hardening observed. This ductility minimum does not need exclusively through the actual precipitation hardening mechanism. On certain contribution to embrittlement can also be obtained by segregation of Contamination to the grain boundaries or possibly through Proximity settings can be provided by dissolved alloy atoms.
  • Excretions on sub-grain boundaries are subject to accelerated coarsening and tend to coagulate with neighboring excretions. Coarse and coagulated Phases generate breakage-causing voltage peaks, which increase ductility reduce. Above all, however, the uneven distribution of the Excretions also the most effective at high temperatures Hardening mechanism, namely particle hardening, severely limited.
  • a ductility increase limited in its effect is due to a reduction the grain size possible. However, this is the case with those known in the art Alloys in large components are difficult to implement using forging technology leaves little effect.
  • a somewhat more important measure for This is an increase in ductility in conventional, martensitic hardenable steels Alloying of nickel.
  • the causes of this are not all Known points and are likely to depend heavily on the nickel content. So small ones Proportions of nickel can be very ductile, if that means about Formation of delta ferrite can be completely suppressed.
  • the Ac1 temperature (this is the one) is above 2% by weight Temperature at which ferrite converts to austenite during heating starts) to temperatures below 700 ° C.
  • Cobalt is an austenite-stabilizing element similar to nickel. In fixed Solution is therefore an effect similar to nickel in terms of ductility expect. From the chemical point of view, however, is an important one Make a difference than that cobalt supports ferromagnetism, the Curie temperature increases. Because the self-diffusion within the iron matrix increases suddenly when the Curie temperature is exceeded Exceeding the Curie temperature all diffusion-controlled recreational and Coarsening processes accelerated. By increasing the Curie temperature an improvement in tempering resistance can therefore be expected. Cobalt alloy structures should then be used during the tempering treatment delayed softening and thus the setting of increased strength enable. Also of importance is the fact that cobalt is the Ac1 temperature per weight percent alloy additive significantly less than Nickel.
  • manganese is on the left next to that Element iron in the periodic system of the elements. It is a Electron-poorer element, which clearly shows its effect in solid solution should be different from nickel and cobalt. Nonetheless, it is a austenite-stabilizing element, which lowers the Ac1 temperature, however not a particularly positive, but rather an unfavorable effect on ductility leaves.
  • the Element manganese therefore comes in particularly in steels containing high levels of nitrogen significant role too because it like the solubility for nitrogen in the melt also increased in the austenite matrix.
  • Manganese also has the property that it is the Austenite-ferrite transformation transition nose at longer times shifts. These properties of manganese result in favorable ones
  • the vanadium nitrides are still required after a solution heat treatment before the martensitic transformation in the area of metastable austenite to leave again.
  • manganese is understood as an impurity element which Promotes embrittlement significantly. Therefore, the manganese content, especially with regard to applications in the temperature range between 350 and 500 ° C, usually limited to very small quantities.
  • the alloy is sufficiently high Apply solubility for preferred levels of nitrogen. It is known, that manganese increases solubility for nitrogen and nickel increases solubility for Nitrogen lowers.
  • the particular advantage of the desired alloy design is that the required solubility for nitrogen is already due to the Element Vanadium is offered, which is necessary for the formation of an optimal structure in an almost stoichiometric ratio to nitrogen is added.
  • the dominant effect of vanadium on the solubility of nitrogen makes it possible that the increased and preferred levels of nitrogen due to Vanadium and almost stoichiometric to vanadium without the use of Overpressure can be introduced and therefore only subordinate to the Presence of nickel and cobalt are impaired.
  • the element cobalt also offers the possibility of aging Without delaying nitrides and the recovery of dislocations when starting that an increased austenite reversion is provoked when starting.
  • a chromium content of 9-13% enables good hardenability thick-walled components and provides sufficient resistance to oxidation up to a temperature of 550 ° C safely.
  • a weight percentage below 9% is impaired through remuneration.
  • Levels above 13% lead to accelerated education of hexagonal chrome nitrides during the tempering process, which besides Nitrogen also binds vanadium, and thus the effectiveness of curing with vanadium nitrides.
  • the optimal chromium content is 10.5 to 11.5%.
  • the area should take into account the ladle metallurgical possibilities in the range between 0.001 and 0.25% for manganese and between 0.001 and 0.15 % for silicon.
  • Nickel is used as an austenite stabilizing element to suppress delta ferrite used. In addition, it is said to be a resolved element in the ferritic matrix improve ductility. Nickel contents up to about 3.5% by weight remain homogeneously dissolved in the matrix if the tempering temperature, or the stress relieving temperature at the end of the whole Remuneration treatment does not exceed 600 ° C. For alloys which low temperatures, i.e. at 600 to 640 ° C preferred nickel content at 3 to 4 wt .-% before. Nickel contents above 4% by weight strengthen the austenite stability in such a way that after solution annealing and Annealing an increased proportion of residual austenite or tempering austenite in tempered martensite.
  • nitrogen and vanadium are suitable for those with high nickel content Steel on a special heat treatment.
  • reaustenitization at temperatures between 700 and 850 ° C allows a re-excretion of vanadium nitrides, which the martensite start temperature can be raised again so that a complete Reconversion to martensite becomes possible again by quenching.
  • Such low reaustenitization temperatures prevent premature Aging of the vanadium nitrides so that they are still an essential one Particle hardening contribution to deliver.
  • Vanadium nitrides form well-stabilized martensite, which is characterized by the preceding grain formation process the setting of a particularly high Ductility enables.
  • Another tempering treatment at about 600 ° C leads to Formation of small austenite islands, which are opposed to a reverse transformation in the martensite is sufficiently stabilized.
  • the volume fraction of this austenite is below 5%, provided the nickel content does not exceed 7%. Even higher Volume fractions increase the risk of embrittlement in one Long-term aging at elevated temperatures.
  • That kind of Heat treatment is suitable for alloys with 2 to 7% nickel.
  • a particularly good combination of heat resistance and ductility is under Consideration of this special heat treatment technology with nickel contents achieved in the range between 4.5 and 6.5%.
  • This element is used as a substitute element for iron in solid solution for the final fine-tuning of ductility and heat resistance used.
  • a weight percentage of up to 10% cobalt can be added without any Austenite transformation at tempering temperatures in the range from 600 to 650 ° C is expected.
  • the optimal cobalt content depends on the proportion of molybdenum and tungsten. This proves to be above about 8% by weight Alloying cobalt as uneconomical.
  • a preferred range of alloys which takes into account the high alloying costs of cobalt, is 3.5 to 4.5% by weight.
  • Molybdenum becomes due to its higher solubility compared to tungsten prefers.
  • a preferred range is by a molybdenum content in the range of 1 to 2% and a tungsten content of less than 1%.
  • Better is one Molybdenum content from 1 to 2.5% and a tungsten content of less than 0.5%.
  • a particularly preferred range is due to a negligibly small one Tungsten content, but given molybdenum contents of 1 to 3%.
  • the Microstructure formation forms are optimal if the elements vanadium and Nitrogen are alloyed in an almost stoichiometric ratio to each other.
  • the ideal weight ratio V / N is 3.6. Because the nitrogen solubility Vanadium is a slightly overstoichiometric V / N To strive for relationship. A slightly over-stoichiometric ratio increased sometimes the stability of the vanadium nitride with respect to the chromium nitride.
  • a V / N ratio in the range between 3.5 to 4.2 is preferred. On a particularly preferred range is 3.8 to 4.2.
  • the concrete content of Nitrogen and vanadium nitrides are based on the optimal volume fraction the vanadium nitrides, which are insoluble during solution treatment Primary nitrides should remain.
  • the positive influence of grain refinement on ductility is limited, however, because with increasing volume fraction of primary nitrides the primary nitrides themselves Limit ductility.
  • the preferred nitrogen content is in the range 0.13 to 0.18% by weight and that of vanadium is in the range between 0.5 and 0.8 % By weight.
  • Titanium nitride is a sparingly soluble nitride that supports grain refinement. In contrast to vanadium nitride, however, it can already be found in the melting and form in particular in the solidification phase, with which the solidification as a whole calmer and finer. Too high proportions of weight lead to very large ones Primary nitrides that worsen ductility. Therefore the top one Titanium content can be limited to 0.05%.
  • Niobium, tantalum, zircon and hafnium are Niobium, tantalum, zircon and hafnium:
  • nitride formers that support the grain refining effect. In order to keep the volume share of the primary nitrides small, their total share must limited to 0.1%.
  • a particularly preferred nitride former is niobium, because Niobium dissolves in small amounts in the vanadium nitride and thus the stability of the Vanadium nitride can improve. Niobium is preferred in the range between 0.01 and 0.07%.
  • This element is a strong nitride generator, which nitrogen is already in the Melt sets and thus the effectiveness of the added nitrogen is strong impaired.
  • the aluminum nitrides formed in the melt are very coarse and lower ductility. Aluminum must therefore have a weight fraction of Be limited to 0.01%.
  • the carbon content should therefore be capped at 0.1%.
  • Another disadvantage is that The fact that carbon increases the hardening during welding.
  • the particularly preferred carbon content is in the range between 0.02 and 0.07 % By weight.
  • Table 1 shows a number of alloys according to the invention.
  • FIG. 1 shows AP28M for 3 different alloys according to the invention, "alloy D “and” alloy E “, which are all alloyed with 4% by weight cobalt and are otherwise mainly differ in nickel content, the adjustable Combination of yield strength at room temperature and transition temperature appearance (FATT).
  • the results will be one with those commercial alloy of the type X12 CrNiMo12 compared, which at 1060 ° C solution annealed, tempered at 640 ° C and stress relieved at 600 ° C has been. Basically, it can be seen that the alloys selected improved yield strength values and / or ductility can be achieved.
  • a simple heat treatment related (W2: 1080 ° C / 640 ° C / 600 ° C) an optimal combination of Heat resistance and ductility with nickel contents in the range between 3 and 3.5% achieved.
  • An exceptionally good combination of yield strength and ductility can be used in particular with high - nickel alloys ("alloy E") set a two-stage austenitizing treatment at 1180 and 750 ° C. This favorable combination of properties is due to the low Ac3 temperature of the Allows high-nickel alloy. For example, it can be assumed that in Alloys with nickel contents of 5.5% by weight almost complete the matrix at 750 ° C is completely austenitic.
  • Figure 2 shows the effect of cobalt on the Combination of yield strength at room temperature and the FATT transition temperature.
  • various heat treatments with solution annealing temperatures between 1080 and 1200 ° C, tempering temperatures between 640 and 750 ° C and one final stress relieving treatment at 600 ° C.
  • solution annealing temperatures between 1080 and 1200 ° C
  • tempering temperatures between 640 and 750 ° C
  • one final stress relieving treatment at 600 ° C.
  • All alloy with low cobalt contents in the lower Quadrants with low yield strength values and high FATT values are therefore similar alloys with increased cobalt contents in terms of the adjustable Combination of yield strength and ductility are clearly inferior.
  • Figures 4 and 5 show graphical representations in which the yield point the alloys "alloy D” and “alloy E” depending on the performed heat treatment is plotted against the test temperature. Furthermore, the yield strengths of the comparative alloys are X12CrNiMo12 (matensitically hardenable steel) and IN706 (precipitation hardenable alloy), and their notch impact work Av compared to the inventive Alloys drawn. It can be seen that for the inventive Alloys “alloy D” and “alloy E” improve the heat resistance up to high test temperatures regardless of the heat treatment and independent of the nickel content is retained. The new alloys according to the invention show in comparison with austenitic high temperature alloys (IN706), which are designed on a nickel-iron basis, an extraordinarily good one Combination of impact energy at room temperature and heat resistance at 550 ° C.
  • I706 austenitic high temperature alloys

Landscapes

  • 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)
  • Heat Treatment Of Articles (AREA)
  • Heat Treatment Of Steel (AREA)
EP01108810A 2000-05-24 2001-04-07 Acier de traitement thermique durcissable martensitique à résistance thermique ameliorée et à ductilité ameliorée Expired - Lifetime EP1158067B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE10025808A DE10025808A1 (de) 2000-05-24 2000-05-24 Martensitisch-härtbarer Vergütungsstahl mit verbesserter Warmfestigkeit und Duktilität
DE10025808 2000-05-24

Publications (2)

Publication Number Publication Date
EP1158067A1 true EP1158067A1 (fr) 2001-11-28
EP1158067B1 EP1158067B1 (fr) 2007-10-17

Family

ID=7643463

Family Applications (1)

Application Number Title Priority Date Filing Date
EP01108810A Expired - Lifetime EP1158067B1 (fr) 2000-05-24 2001-04-07 Acier de traitement thermique durcissable martensitique à résistance thermique ameliorée et à ductilité ameliorée

Country Status (4)

Country Link
US (1) US6464804B2 (fr)
EP (1) EP1158067B1 (fr)
JP (1) JP2002004012A (fr)
DE (2) DE10025808A1 (fr)

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2008116582A1 (fr) * 2007-03-26 2008-10-02 Ejot Baubefestigungen Gmbh Vis autofiletante comportant une tige en acier inoxydable et une pointe dure jointe à la tige
WO2008119638A1 (fr) * 2007-03-29 2008-10-09 Alstom Technology Ltd Acier résistant au fluage
EP2116626A1 (fr) 2008-02-25 2009-11-11 ALSTOM Technology Ltd Acier resistant au fluage
US7686898B2 (en) 2004-10-29 2010-03-30 Alstom Technology Ltd Creep-resistant maraging heat-treatment steel
CN108546883A (zh) * 2018-06-13 2018-09-18 唐山东方华盛优耐高科股份有限公司 低成本高韧性异质合金耐磨锤头及其制造方法
CN110846563A (zh) * 2019-09-27 2020-02-28 无锡宏达重工股份有限公司 X12CrMoWVNbN10-1-1晶粒细化的热处理工艺

Families Citing this family (20)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE10033471C1 (de) * 2000-07-10 2001-12-06 Sfs Ind Holding Ag Heerbrugg Selbstbohrender Befestiger
DE10063117A1 (de) * 2000-12-18 2003-06-18 Alstom Switzerland Ltd Umwandlungskontrollierter Nitrid-ausscheidungshärtender Vergütungsstahl
JP3905739B2 (ja) * 2001-10-25 2007-04-18 三菱重工業株式会社 タービンロータ用１２Ｃｒ合金鋼、その製造方法及びタービンロータ
US7604680B2 (en) * 2004-03-31 2009-10-20 General Electric Company Producing nickel-base, cobalt-base, iron-base, iron-nickel-base, or iron-nickel-cobalt-base alloy articles by reduction of nonmetallic precursor compounds and melting
US7922065B2 (en) 2004-08-02 2011-04-12 Ati Properties, Inc. Corrosion resistant fluid conducting parts, methods of making corrosion resistant fluid conducting parts and equipment and parts replacement methods utilizing corrosion resistant fluid conducting parts
DE102008049055B4 (de) * 2008-09-26 2010-08-05 Lufthansa Technik Ag Verfahren zur Reparatur eines Gehäuseflanschs eines Flugzeugtriebwerks
US20100236317A1 (en) * 2009-03-19 2010-09-23 Sigelko Jeff D Method for forming articles at an elevated temperature
DE102009035111B4 (de) * 2009-07-29 2022-11-03 Schaeffler Technologies AG & Co. KG Windkraftanlage mit einem Wälzlagerbauteil
US9375771B2 (en) 2009-08-17 2016-06-28 Ati Properties, Inc. Method of producing cold-worked centrifugal cast tubular products
US9574684B1 (en) 2009-08-17 2017-02-21 Ati Properties Llc Method for producing cold-worked centrifugal cast composite tubular products
US8479549B1 (en) * 2009-08-17 2013-07-09 Dynamic Flowform Corp. Method of producing cold-worked centrifugal cast tubular products
US10118259B1 (en) 2012-12-11 2018-11-06 Ati Properties Llc Corrosion resistant bimetallic tube manufactured by a two-step process
CN107208219A (zh) * 2015-02-25 2017-09-26 日立金属株式会社 热作工具及其制造方法
GB2546809B (en) * 2016-02-01 2018-05-09 Rolls Royce Plc Low cobalt hard facing alloy
GB2546808B (en) * 2016-02-01 2018-09-12 Rolls Royce Plc Low cobalt hard facing alloy
CN106947922A (zh) * 2017-03-13 2017-07-14 浙江工贸职业技术学院 一种马氏体钢及其结构硬化处理方法
US20200165709A1 (en) * 2017-09-21 2020-05-28 Mitsubishi Hitachi Power Systems, Ltd. Gas turbine disk material and heat treatment method therefor
DE102020205697A1 (de) 2020-05-06 2021-11-11 Robert Bosch Gesellschaft mit beschränkter Haftung Nichtrostender martensitisch härtbarer Stahl für hochbeanspruchte Bauteile und Verfahren zur Herstellung derartiger Bauteile
CN111575583A (zh) * 2020-05-18 2020-08-25 江苏联峰实业有限公司 一种高强度的热轧型材及其控温控冷工艺
CN113943849B (zh) * 2021-10-18 2023-05-05 华能国际电力股份有限公司 一种高铬耐热合金的热处理工艺

Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB741935A (en) * 1952-08-22 1955-12-14 Hadfields Ltd Improvements in alloy steels
JPH05263196A (ja) * 1992-03-19 1993-10-12 Nippon Steel Corp 高温強度ならびに靱性に優れたフェライト系耐熱鋼
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
EP0688883A1 (fr) * 1993-12-28 1995-12-27 Nippon Steel Corporation Acier thermo-resistant martensitique dote d'une excellente resistance a l'adoucissement des zones affectees thermiquement et procede de production correspondant
JPH08225833A (ja) * 1995-02-16 1996-09-03 Nippon Steel Corp 高温クリープ強度の優れたマルテンサイト系耐熱鋼の製造方法
EP0866145A2 (fr) * 1997-03-21 1998-09-23 Abb Research Ltd. Alliage d'acier complètement martensitique
EP0931845A1 (fr) * 1998-01-27 1999-07-28 Mitsubishi Heavy Industries, Ltd. Matériau pour disque de turbine à gaz

Family Cites Families (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2905577A (en) * 1956-01-05 1959-09-22 Birmingham Small Arms Co Ltd Creep resistant chromium steel
JP3032273B2 (ja) * 1990-10-16 2000-04-10 日新製鋼株式会社 高強度スチールベルトの製造方法
WO1995020683A1 (fr) * 1994-01-26 1995-08-03 Kawasaki Steel Corporation Procede de production de tole d'acier inoxydable a haute resistance a la corrosion
US5820817A (en) * 1997-07-28 1998-10-13 General Electric Company Steel alloy

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB741935A (en) * 1952-08-22 1955-12-14 Hadfields Ltd Improvements in alloy steels
JPH05263196A (ja) * 1992-03-19 1993-10-12 Nippon Steel Corp 高温強度ならびに靱性に優れたフェライト系耐熱鋼
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
EP0688883A1 (fr) * 1993-12-28 1995-12-27 Nippon Steel Corporation Acier thermo-resistant martensitique dote d'une excellente resistance a l'adoucissement des zones affectees thermiquement et procede de production correspondant
JPH08225833A (ja) * 1995-02-16 1996-09-03 Nippon Steel Corp 高温クリープ強度の優れたマルテンサイト系耐熱鋼の製造方法
EP0866145A2 (fr) * 1997-03-21 1998-09-23 Abb Research Ltd. Alliage d'acier complètement martensitique
EP0931845A1 (fr) * 1998-01-27 1999-07-28 Mitsubishi Heavy Industries, Ltd. Matériau pour disque de turbine à gaz

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
PATENT ABSTRACTS OF JAPAN vol. 018, no. 040 (C - 1155) 21 January 1994 (1994-01-21) *
PATENT ABSTRACTS OF JAPAN vol. 1997, no. 01 31 January 1997 (1997-01-31) *

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US7686898B2 (en) 2004-10-29 2010-03-30 Alstom Technology Ltd Creep-resistant maraging heat-treatment steel
WO2008116582A1 (fr) * 2007-03-26 2008-10-02 Ejot Baubefestigungen Gmbh Vis autofiletante comportant une tige en acier inoxydable et une pointe dure jointe à la tige
WO2008119638A1 (fr) * 2007-03-29 2008-10-09 Alstom Technology Ltd Acier résistant au fluage
US8147748B2 (en) 2007-03-29 2012-04-03 Alstom Technology Ltd. Creep-resistant steel
EP2116626A1 (fr) 2008-02-25 2009-11-11 ALSTOM Technology Ltd Acier resistant au fluage
CN108546883A (zh) * 2018-06-13 2018-09-18 唐山东方华盛优耐高科股份有限公司 低成本高韧性异质合金耐磨锤头及其制造方法
CN108546883B (zh) * 2018-06-13 2019-12-24 唐山东方华盛优耐高科股份有限公司 低成本高韧性异质合金耐磨锤头及其制造方法
CN110846563A (zh) * 2019-09-27 2020-02-28 无锡宏达重工股份有限公司 X12CrMoWVNbN10-1-1晶粒细化的热处理工艺

Also Published As

Publication number Publication date
US6464804B2 (en) 2002-10-15
DE10025808A1 (de) 2001-11-29
JP2002004012A (ja) 2002-01-09
US20020003008A1 (en) 2002-01-10
DE50113134D1 (de) 2007-11-29
EP1158067B1 (fr) 2007-10-17

Similar Documents

Publication Publication Date Title
EP1158067B1 (fr) Acier de traitement thermique durcissable martensitique à résistance thermique ameliorée et à ductilité ameliorée
AT394056B (de) Verfahren zur herstellung von stahl
WO2019121879A1 (fr) Procédé de fabrication additive d'un objet à partir d'une poudre d'acier maraging
DE60300561T3 (de) Verfahren zur Herstellung eines warmgewalzten Stahlbandes
DE60115232T2 (de) Stahllegierung, werkzeug zum plastiggiessen und zähgehärteter rohling für plastikgiesswerkzeuge
EP1805340B1 (fr) Acier de traitement martensitique, durcissable et resistant au fluage
DE19712020A1 (de) Vollmartensitische Stahllegierung
DE3310693C2 (fr)
DE1301586B (de) Austenitische ausscheidungshaertbare Stahllegierung und Verfahren zu ihrer Waermebehandlung
EP3899064B1 (fr) Matériau superausténitique
EP2240619B1 (fr) Acier résistant au fluage
WO2020064127A1 (fr) Alliage à mémoire de forme, produit plat en acier préparé à partir de celui-ci doté de caractéristiques pseudoélastiques et procédé pour la préparation d'un tel produit plat en acier
EP1215299B1 (fr) Acier de traitment à durcissement par precipitation des nitrides et à transformation controllée
EP3847284B1 (fr) Produit plat laminé à chaud en acier et procédé de fabrication
EP1255873B9 (fr) Acier a ressorts de type acier vieilli thermiquement
DE10124393B4 (de) Hitzebeständiger Stahl, Verfahren zur thermischen Behandlung von hitzebeständigem Stahl, und Kompenten aus hitzebeständigem Stahl
EP2116626B1 (fr) Acier resistant au fluage
DE60126646T2 (de) Stahllegierung, halter und haltereinzelteile für kunststoff-formwerkzeuge und vergütete rohlinge für halter und haltereinzelteile
EP0733719B1 (fr) Alliage à base de fer pour applications aux températures élevées
EP0897018A1 (fr) Acier inoxydable duplex présentant une amélioration de résistance mécanique et de résistance à la corrosion
EP3225702A1 (fr) Acier a epaisseur reduite et procede de fabrication d'un produit allonge ou plat en acier a partir d'un tel acier
EP1445339B1 (fr) Alliage et article à haute résistance thermique et à haute stabilité thermique
DE102018108173A1 (de) Austenitische Legierung und Verfahren zum Herstellen einer stickstoffhaltigen austenitischen Legierung
WO2004033741A1 (fr) Tete de baton de golf en acier maraging
DE112023000190T5 (de) Ausscheidungshärtender weichmagnetischer ferritischer Edelstahl mit hervorragender Zerspanbarkeit

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AT BE CH CY DE DK ES FI FR GB GR IE IT LI LU MC NL PT SE TR

Kind code of ref document: A1

Designated state(s): DE GB

AX Request for extension of the european patent

Free format text: AL;LT;LV;MK;RO;SI

RAP1 Party data changed (applicant data changed or rights of an application transferred)

Owner name: ALSTOM (SWITZERLAND) LTD

RAP1 Party data changed (applicant data changed or rights of an application transferred)

Owner name: ALSTOM (SWITZERLAND) LTD

17P Request for examination filed

Effective date: 20020410

AKX Designation fees paid

Free format text: DE GB

RAP1 Party data changed (applicant data changed or rights of an application transferred)

Owner name: ALSTOM TECHNOLOGY LTD

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): DE GB

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

Free format text: NOT ENGLISH

REF Corresponds to:

Ref document number: 50113134

Country of ref document: DE

Date of ref document: 20071129

Kind code of ref document: P

GBT Gb: translation of ep patent filed (gb section 77(6)(a)/1977)

Effective date: 20080130

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

26N No opposition filed

Effective date: 20080718

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: GB

Payment date: 20110328

Year of fee payment: 11

Ref country code: DE

Payment date: 20110429

Year of fee payment: 11

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20120407

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20120407

REG Reference to a national code

Ref country code: DE

Ref legal event code: R119

Ref document number: 50113134

Country of ref document: DE

Effective date: 20121101

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: DE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20121101