EP1420077B1 - Reaktionsträger Werkstoff mit erhöhter Härte für thermisch beanspruchte Bauteile - Google Patents

Reaktionsträger Werkstoff mit erhöhter Härte für thermisch beanspruchte Bauteile Download PDF

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Publication number
EP1420077B1
EP1420077B1 EP02450262A EP02450262A EP1420077B1 EP 1420077 B1 EP1420077 B1 EP 1420077B1 EP 02450262 A EP02450262 A EP 02450262A EP 02450262 A EP02450262 A EP 02450262A EP 1420077 B1 EP1420077 B1 EP 1420077B1
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EP
European Patent Office
Prior art keywords
minus
alloy
nickel
hardness
weight
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 - Lifetime
Application number
EP02450262A
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German (de)
English (en)
French (fr)
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EP1420077A1 (de
Inventor
Gottfried Mayerböck
Johann Sammler
Gabriele Saller
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.)
Voestalpine Boehler Edelstahl GmbH
Original Assignee
Boehler Edelstahl GmbH
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Filing date
Publication date
Application filed by Boehler Edelstahl GmbH filed Critical Boehler Edelstahl GmbH
Priority to SI200230449T priority Critical patent/SI1420077T1/sl
Priority to AT02450262T priority patent/ATE341651T1/de
Publication of EP1420077A1 publication Critical patent/EP1420077A1/de
Application granted granted Critical
Publication of EP1420077B1 publication Critical patent/EP1420077B1/de
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

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    • 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
    • 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
    • C22C38/001—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
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
    • 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
    • C22C38/50—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
    • 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
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • 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
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment

Definitions

  • the invention relates to a material with high inertness, in particular high oxidation resistance and increased hardness for thermally resilient components and tools.
  • a reaction of a metallic material with its surroundings which causes a measurable change in the material, is defined as corrosion.
  • Corrosion can be done with and without mechanical stress of the component, as well as after various types of chemical attack and at different temperatures.
  • Corrosion-resistant and heat-resistant steels and alloys are also said to have a cubic face-centered atomic lattice structure or an austenitic microstructure due to their thermal stability at temperatures above 600 ° C.
  • this means that such materials have higher nickel and / or cobalt contents or, in view of increased strength and hardness at high temperatures, are in the form of nickel-base or cobalt-base alloys, although from corrosion-chemical Due to a chromium content of at least greater than 13 wt .-% must be present.
  • JP2001011583A discloses an austenitic heat-resistant steel having particular high-temperature strength for steam boiler tubes, which steel has a limited chromium equivalent and thereby no tendency to embrittlement by precipitates of sigma phase in long-term use. However, this material has a low strength and a low 0.2% yield strength at 650 ° C.
  • an austenitic iron-base material with a nickel content of less than 36% by weight can certainly withstand a corrosion attack at high temperatures, for example at 600 ° C. and above, over a required minimum period of time owing to a high chromium concentration, if appropriate in combination with other corrosion-inhibiting elements
  • the material has a low hardness and a similar strength and a limited creep behavior.
  • alloys according to DIN material no. 1.2780 and 1.2782 and 1.2786 are used for reasons of economy and for reasons of production as tools for glass processing.
  • the invention seeks to remedy the situation and sets itself the goal of specifying a material of the type mentioned above with a hardness of greater than 230 HB, which also at temperatures above 600 ° C high creep resistance and improved creep behavior and a similar corrosion resistance having.
  • the invention aims at the use of an iron-based alloy as a material for hot working tools, which are used at working temperatures of about 550 ° C from.
  • the aforementioned object is achieved in a material of the type mentioned, consisting of an alloy with a composition in wt .-% of Carbon (C) 0.04 to 0.15 Silicon (Si) 1.22 to 2.36 Manganese (Mn) 1.0 to 3.95 Chrome (Cr) 23.9 to 26.5 Nickel (Ni) 17.9 to 25.45 Nitrogen (N) 0.018 to 0.2 with the proviso that the nickel content of the alloy is equal to or greater than the value formed by the content of chromium plus 1.5 silicon minus 0.12 manganese minus 18 nitrogen minus 30 carbon minus the numerical value 6 Ni ⁇ Cr + 1 . 5 ⁇ Si - 0 .
  • Mo Molybdenum
  • Mo Molybdenum
  • V Vanadium
  • W Tungsten
  • Cu Copper
  • Co Cobalt
  • Co Co
  • Ti Titanium
  • Niobium Nb
  • Fe Remainder iron
  • the advantages achieved by the invention are in particular the synergy of corrosion resistance of the selected alloy and the achievable in this chemical composition by means of cold forming properties of the material.
  • solidification of the material takes place by blocking dislocations in the crystal lattice.
  • An associated increase in hardness and an increase in the strength of the material according to the invention remains, surprising for the expert, even at use temperatures of over 600 ° C, the expected recoveries in the strained grid, such as a thermally activated cross sliding and recombining dislocations can in usual Periods are not observed.
  • the nickel and chromium concentration specified in limits and by the limited concentration range of nickel as a function of chromium, silicon, manganese, nitrogen and carbon. Higher nickel levels have been found to degrade creep behavior. On the other hand, at low nickel concentrations the austenite stability and the heat resistance of the material are abruptly reduced. Essentially the same applies to the elements carbon and nitrogen, in particular nitrogen increases the fatigue strength of the material.
  • Impurities can of course deteriorate the material properties, so that the alloy according to the invention for the impurity elements concentration values in wt .-% of Oxygen (O) max 0.05 Phosphorus (P) max 0.03 Sulfur (S) max 0.03 having.
  • the object of the invention is a method for producing a material for components and tools with high inertia, in particular high oxidation resistance and increased hardness under thermal stress at a temperature of up to 750 ° C, after which from an alloy having a composition in wt.
  • Ni 17.9 to 25.45
  • Mo Molybdenum
  • Mo Molybdenum
  • V Vanadium
  • W Tungsten
  • Cu Copper
  • Co Cobalt
  • Co Co
  • Ti Titanium
  • Niobium Nb
  • Residual iron Fe
  • the elastic limit of the material can be raised to a voltage level which is not reached near the working surface of the component or tool in a volume change due to alternating thermal load. Accordingly, even in the area of the grain boundaries, no zones which are plastically deformed during the temperature change occur, whereby cracking due to material fatigue can be avoided. Thus, a grain boundary attack by chemical or hot corrosion is largely avoidable, so that, as for example in a glass mold, a high Hävid- or surface quality is maintained even at high loads and large quantities of production over a long time.
  • Conventional glass molds often show after a short period of use at the grain boundaries of the structure material erosion, which have a distance in the range of a few microns. As a result, the shaped glass is imparted with unevennesses in the lightwave area, which may result in reflection interference and frosted glass effects.
  • the corrosion and the heat resistance can be further increased and fatigue cracking can be effectively suppressed if, according to the invention by cold working, a material with a hardness greater than 250 HB, in particular of 300 HB and higher is formed.
  • a precursor having a composition of the invention is formed by hot working, subjected to a solution annealing treatment, or thermoformed, cooled, and cold worked from the deformation temperature, a particularly pattern-homogenous material having improved corrosion resistance can be prepared.
  • substantially axially symmetric shaped tools such as bottle molds and the like
  • the further object of the invention is achieved when using an iron-based alloy with alloying elements in wt .-% of Carbon (C) 0.04 to 0.15 Silicon (Si) 1.22 to 2.36 Manganese (Mn) 1.0 to 3.95 Chrome (Cr) 23.9 to 26.5 Nickel (Ni) 17.9 to 25.45 Nitrogen (N) 0.018 to 0.2 with the proviso that the nickel content of the alloy is equal to or greater than the value formed by the content of chromium plus 1.5 silicon minus 0.12 manganese minus 18 nitrogen minus 30 carbon minus the numerical value 6 Ni ⁇ Cr + 1 . 5 ⁇ Si - 0 .
  • Mo Molybdenum
  • Mo Molybdenum
  • V Vanadium
  • W Tungsten
  • Cu Copper
  • Co Cobalt
  • Co Co
  • Ti Titanium
  • Ni Niobium
  • Fe Residual iron
  • impurities which alloy by cold deformation of more than 6% of the precursor formed therefrom to a material hardness of greater than 230 HB, preferably greater than 250 HB, solidified as a material for hot working tools in the glass industry, especially as a mold material for machine press glasses with a working temperature higher than 555 ° C, preferably higher than 602 ° C, especially up to 750 ° C.
  • Fig. 1 strength as a function of the degree of cold deformation of a material according to the invention at 604 ° C.
  • Fig. 2 hardness curve at room temperature after a long-term temperature stress at 600 ° C.
  • Fig. 1 the strength of the material according to the invention is shown at a test temperature of 604 ° C, depending on the extent of cold working.
  • the sample material was forged at a temperature of 1010 ° C and increasingly cooled from the forming heat and subjected to solution annealing treatment at 1060 ° C. Each part of the material was cold worked with a degree of deformation of 21%, 35%, 47% and 55%, after which tensile tests were made.
  • the strength determinations namely 0.2% proof strength and tensile strength, were made at a temperature of 604 ° C with the samples kept at that temperature for 20 minutes.
  • standard material was solution heat treated at 1060 ° C and samples made from it were also tested at 604 ° C.
  • the bar graph of FIG. 1 clearly shows an increase in the strength values of the material as a function of the degree of deformation, wherein (not shown in the diagram) an increase in strength is given to a great extent already at a cold deformation degree of more than 6%, in particular greater than 12% ,
  • the sample material was solution heat treated at 1060 ° C. followed by quenching in water, after which samples designated H 5 were undeformed and samples designated H 525 were subjected to long-term annealing at 600 ° C. with a cold working of 35%.
  • the comparative materials No. 1.2083 and No. 1.4028 were hardened from 1020 ° C in oil, tempered at 630 ° C and also subjected to the long-term annealing. After 45, 90, 140, and 180 hours, the sample material was removed from the oven, allowed to cool, and the hardness of the material tested, followed by back-loading of the samples (with thermal cycling).
  • the comparison material H 5 showed an expected behavior of the hardness, whereas the 35% cold-worked material H 525 according to the invention had an increased hardness of 315 HB and a high creep behavior. At 600 ° C no hardness reduction and no creep of the material could be determined even with changing thermal load. In contrast, the martensitic standard steels showed a marked decrease in hardness with the annealing time of the samples.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Articles (AREA)
  • Moulds For Moulding Plastics Or The Like (AREA)
  • Powder Metallurgy (AREA)
  • Organic Low-Molecular-Weight Compounds And Preparation Thereof (AREA)
  • Catalysts (AREA)
  • Contacts (AREA)
EP02450262A 2002-01-23 2002-11-15 Reaktionsträger Werkstoff mit erhöhter Härte für thermisch beanspruchte Bauteile Expired - Lifetime EP1420077B1 (de)

Priority Applications (2)

Application Number Priority Date Filing Date Title
SI200230449T SI1420077T1 (sl) 2002-01-23 2002-11-15 Trd inerten material za toplotno obremenjene dele
AT02450262T ATE341651T1 (de) 2002-01-23 2002-11-15 Reaktionsträger werkstoff mit erhöhter härte für thermisch beanspruchte bauteile

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
AT0010702A AT410550B (de) 2002-01-23 2002-01-23 Reaktionsträger werkstoff mit erhöhter härte für thermisch beanspruchte bauteile

Publications (2)

Publication Number Publication Date
EP1420077A1 EP1420077A1 (de) 2004-05-19
EP1420077B1 true EP1420077B1 (de) 2006-10-04

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EP02450262A Expired - Lifetime EP1420077B1 (de) 2002-01-23 2002-11-15 Reaktionsträger Werkstoff mit erhöhter Härte für thermisch beanspruchte Bauteile

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Country Link
US (1) US20030136482A1 (da)
EP (1) EP1420077B1 (da)
KR (1) KR100540851B1 (da)
CN (1) CN1434146A (da)
AT (1) AT410550B (da)
BR (1) BR0300116A (da)
CA (1) CA2416950C (da)
DE (1) DE50208351D1 (da)
DK (1) DK1420077T3 (da)
ES (1) ES2273992T3 (da)
RU (1) RU2246553C2 (da)
TW (1) TWI225102B (da)

Families Citing this family (15)

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EP1605072B1 (en) * 2003-03-20 2012-09-12 Sumitomo Metal Industries, Ltd. Stainless steel for high pressure hydrogen gas, vessel and equipment comprising the steel
US20090053100A1 (en) * 2005-12-07 2009-02-26 Pankiw Roman I Cast heat-resistant austenitic steel with improved temperature creep properties and balanced alloying element additions and methodology for development of the same
JP4329883B1 (ja) * 2008-02-27 2009-09-09 住友金属工業株式会社 耐浸炭性金属材料
UA100460C2 (uk) * 2008-11-19 2012-12-25 Сандвік Інтеллекчуал Проперті Аб Сплав на основі нікелю, здатний утворювати оксид алюмінію
RU2415962C2 (ru) * 2009-01-11 2011-04-10 Федеральное государственное унитарное предприятие "Государственный космический научно-производственный центр имени М.В. Хруничева" (ФГУП "ГКНПЦ им. М.В. Хруничева") Аустенитная дисперсионно-твердеющая высокопрочная сталь, стойкая к сероводородному растрескиванию под напряжением
ES2418135T3 (es) 2009-02-17 2013-08-12 Mec Holding Gmbh Aleación resistente al desgaste
EP2287351A1 (en) * 2009-07-22 2011-02-23 Arcelormittal Investigación y Desarrollo SL Heat-resistant austenitic steel having high resistance to stress relaxation cracking
CN101921967A (zh) * 2010-08-12 2010-12-22 江苏新华合金电器有限公司 一种新型奥氏体耐热不锈钢
CN102650023A (zh) * 2011-02-23 2012-08-29 宝山钢铁股份有限公司 一种油套管用含铜铁镍铬合金
US9347121B2 (en) * 2011-12-20 2016-05-24 Ati Properties, Inc. High strength, corrosion resistant austenitic alloys
CN110520551B (zh) * 2017-03-03 2022-01-07 博格华纳公司 具有增强的高温抗氧化性的镍和铬基铁合金
ES2864406T3 (es) 2018-07-02 2021-10-13 Hoeganaes Ab Publ Composiciones de alineación a base de hierro resistentes al desgaste que comprenden níquel
CN110724873A (zh) * 2018-07-17 2020-01-24 宝钢特钢有限公司 一种高耐磨模锻模具钢及其制造方法
RU2703318C1 (ru) * 2019-04-15 2019-10-16 Акционерное Общество "Российский Концерн По Производству Электрической И Тепловой Энергии На Атомных Станциях" (Ао "Концерн Росэнергоатом") Радиационно-стойкая аустенитная сталь для внутрикорпусной выгородки ввэр
AT17259U1 (de) * 2020-11-13 2021-10-15 Plansee Se Hochtemperatur-umformwerkzeug

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US5016460A (en) * 1989-12-22 1991-05-21 Inco Alloys International, Inc. Durable method for producing finned tubing
WO2002042510A1 (en) * 2000-11-24 2002-05-30 Sandvik Ab Cylindrical tube for industrial chemical installations

Also Published As

Publication number Publication date
KR100540851B1 (ko) 2006-01-10
ES2273992T3 (es) 2007-05-16
BR0300116A (pt) 2003-09-09
DK1420077T3 (da) 2007-02-05
TWI225102B (en) 2004-12-11
DE50208351D1 (de) 2006-11-16
RU2003101774A (ru) 2005-01-10
RU2246553C2 (ru) 2005-02-20
AT410550B (de) 2003-05-26
HK1067668A1 (zh) 2005-04-15
US20030136482A1 (en) 2003-07-24
CN1434146A (zh) 2003-08-06
CA2416950C (en) 2007-08-28
KR20030064304A (ko) 2003-07-31
EP1420077A1 (de) 2004-05-19
CA2416950A1 (en) 2003-07-23
ATA1072002A (de) 2002-10-15

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