EP1445339B1 - Legierung und Gegenstand mit hoher Warmfestigkeit und hoher thermischer Stabilität - Google Patents

Legierung und Gegenstand mit hoher Warmfestigkeit und hoher thermischer Stabilität Download PDF

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Publication number
EP1445339B1
EP1445339B1 EP04450025.4A EP04450025A EP1445339B1 EP 1445339 B1 EP1445339 B1 EP 1445339B1 EP 04450025 A EP04450025 A EP 04450025A EP 1445339 B1 EP1445339 B1 EP 1445339B1
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EP
European Patent Office
Prior art keywords
alloy
molybdenum
hot
vanadium
hardness
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
EP04450025.4A
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German (de)
English (en)
French (fr)
Other versions
EP1445339A1 (de
Inventor
Devrim Dipl.-Ing. Dr Caliskanoglu
Kay M.Eng. Fisher
Reinhold Univ. Prof. Dipl.-Ing. Dr. Ebner
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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Publication date
Application filed by Boehler Edelstahl GmbH filed Critical Boehler Edelstahl GmbH
Publication of EP1445339A1 publication Critical patent/EP1445339A1/de
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Publication of EP1445339B1 publication Critical patent/EP1445339B1/de
Anticipated expiration legal-status Critical
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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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/52—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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations
    • 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
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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 an alloy for the production of articles with high heat resistance and toughness.
  • the invention relates to a hot work tool steel article having high hardness, high heat resistance and high thermal stability.
  • hot work tool steels can be referred to as thermally recoverable iron-based alloys whose elevated mechanical properties after heat treatment, in particular their high strength and hardness, are maintained up to temperatures of 500 ° C. and above.
  • Conventional hot working steels are carbon-containing iron-based alloys containing 0.3 to 0.4% by weight of carbon (C), the hardness of which is increased as required by quench hardening due to martensite formation in the microstructure and tempering.
  • tungsten (W) to 9 wt .-% and cobalt (Co) to 3.0 wt .-% the use temperature can be slightly increased.
  • the hot hardness of such steels is given by a precipitation mechanism, referred to by those skilled in the art as secondary hardening where the finest chromium-molybdenum-tungsten-vanadium carbides are formed in the martensite lattice , which is, for example, the documents JP 07228945A and US-A-3453151 reveal.
  • an alloyed material is first subjected to a solution annealing treatment followed by increased cooling, with which an alloying additive or phase is completely or partially solubilized and maintained in supersaturated solution. Subsequent heating to a temperature below the solution annealing temperature causes the supersaturation fraction of the element (s) or phase (s) to precipitate, causing a change in material properties, typically a material hardness increase.
  • Precipitation-hardenable iron base materials generally have alloy contents in% by weight of: Carbon (C) to 0.05 Manganese (Mn) to 2.0 Chrome (Cr) to 16.0 Molybdenum (Mo) to 6.0 Nickel (Ni) to 26.0 Vanadin (V) to 0.4 Cobalt (Co) to 10.0 Titanium (Ti) to 3.0 Aluminum (Al) to 0.3
  • the aim of the invention is to provide an alloy which makes it possible to improve the overall property profile of an object made therefrom.
  • a hot work tool article with simultaneously high hardness and high toughness, high heat resistance and high thermal stability can be provided.
  • the object of the invention mentioned above is with an alloy consisting of in wt .-%: Carbon (C) 0.15 to 0.44 Silicon (Si) 0.04 to 0.3 Manganese (Mn) 0.06 to 0.4 Chrome (Cr) 1.2 to 5.0 Molybdenum (Mo) 0.8 to 6.5 Nickel (Ni) 3.4 to 9.8 Vanadin (V) 0.2 to 0.8 Cobalt (Co) 0.1 to 9.8 Aluminum (Al) 1.4 to 3.0 Copper (Cu) under 1.3 Niobium (Nb) under 0.35 Iron (Fe) rest as well as production-related impurities.
  • a hardenability of large parts is improved possible because alloying a corresponding thermal conversion behavior of the material is set.
  • the tempering resistance and thus the thermal stability of the tempered material at high hardness are substantially improved.
  • a carbon content of at least 0.15 wt .-% is provided so that a sufficient amount of carbide for a desired secondary increase in hardness can be eliminated.
  • Higher carbon concentrations than 0.44 wt .-% can interfere with the proposed carbide-forming elements, the toughening reduce primary carbides, so that the content of carbon should be between 0.15 and 0.44 wt .-%.
  • the content of silicon must be an advantageous composition of a deoxidation product because of at least 0.04 wt .-%, on the other hand, however, should not be higher than 0.3 wt .-%, because higher silicon values adversely affect the material toughness.
  • Manganese is provided according to the invention in the steel with a concentration of between 0.06 and 0.4% by weight. Lower levels can cause thermoforming and higher levels of brittleness to harden the material.
  • Chromium contents below 1.2% by weight have a disadvantageous effect on the hardenability of the material; those of more than 5.0% by weight impair the thermal stability of the same, because this suppresses the activity of the molybdenum.
  • the strong carbide Vanadin is provided according to the invention with a minimum content of 0.2 wt .-% to ensure sufficient, stable secondary hardening of the steel sure.
  • niobium is similar to that of vanadium, it is characterized by the formation of very stable carbides, so that the content of niobium should advantageously be below 0.35 wt .-%.
  • the alloy according to the invention thus has a content of chromium of from 1.2 to 5.0, molybdenum, at a carbon concentration of 0.15 to 0.44% by weight 0.8 to 6.5 and on vanadium from 0.2 to 0.8.
  • the nickel concentration of the steel and its aluminum content are to be seen in terms of the precipitation kinetics of the phase of Al Fe 2 Ni for hardness increase in a proposed heat treatment technology. At nickel contents below 3.4 wt .-% and at an aluminum concentration of less than 1.4 wt .-% precipitation hardening is pushed back, so the additive increase in hardness as a material during tempering low.
  • Nickel shift the ⁇ / ⁇ conversion to lower temperatures, which can lead to problems in the soft-annealing treatment of the steel, a high processing hardness and the disruption of the precipitation kinetics.
  • Copper can form undesirable intermetallic phases and should be contained in the steel at a low concentration of less than 1.3% by weight.
  • an alloy which contains one or more of the impurity elements with the following MAXIMUM concentrations in% by weight: Phosphorus (P) 0.02, preferably 0.005 Sulfur (S) 0,008, preferably 0,003 Copper (Cu) 0.15 preferably 0.06 Titanium (Ti) 0.01, preferably 0.005 Niobium (Nb) 0.001, preferably 0.0005 Nitrogen (N) 0,025, preferably 0,015 Oxygen (O) 0.009, preferably 0,002 Calcium (Ca) 0,003, preferably 0.001 Magnesium (Mg) 0,003, preferably 0.001 Tin (Sn) 0.01, preferably 0.005 Tantalum (Ta) 0.001, preferably 0.0005
  • the object of the invention is achieved according to an improved property profile of a hot work tool article when a hot-working and machining primary material prepared by a melt metallurgy or powder metallurgy process having a previously given chemical composition is molded, which molded article becomes secondary after a thermosetting heat treatment precipitated carbides, as well as intermetallic precipitates.
  • the total hardness of the material is advantageously achieved by a superposition of the secondary hardness increase by carbide precipitations and precipitation hardening.
  • high material hardness values can be achieved, although the tempering technology is directed to obtaining high material toughness and using lower hardening temperatures compared to prior art hot work tool steel.
  • This lower austenitizing temperature may also have significant advantages in terms of low distortion in a tempering treatment of complicated shaped parts.
  • the values for high hardness values are Toughness is particularly high and the thermal stability is shifted by up to 50 ° C and more to higher temperatures.
  • a hot work tool according to the invention which secondarily precipitated chromium-molybdenum-vanadium mixed carbides and substantially has intermetallic phases of the type Al Fe 2 Ni in the structure, has a particularly preferred property profile and can be produced economically in conventional hardening equipment at relatively low curing temperatures.
  • the hardness profile of the materials was determined as a function of the temperature. It is essential that the alloy A according to the invention required an austenitizing temperature of 990 ° C. in order to achieve this hardness, but that of 1050 ° C. was required for the conventional hot-rolled steel B, however.
  • the temperature as shown in Tab. 3A and Tab. 3B, increased in the range between 500 ° C and 600 ° C, the hardness of the inventively assembled sample A to values around 60 HRC, whereas in the conventional hot-rolled steel B a maximum Hardness value of 56 HRC at 500 ° C was determined.
  • Fig. 1 the respective hardness curve depending on the temperature of the material A according to the invention and the hot working steel alloy B according to the prior art comparatively shown.
  • a hardness determination on the test specimen at the test temperature was carried out according to the rebound hardness method (Shore hardness), for which return values hitherto only a conversion into Vickers hardness values is present.
  • the alloy A according to the invention In comparison with a conventional hot-work steel B and a maraging steel C, the alloy A according to the invention with the same initial hardness at 650 ° C. for a time of up to 1000 minutes had the highest material hardness. After this time, maraging steel C had a higher hardness with high thermal stability, whereas hot work steel A according to the invention lost about 10% of its hardness up to about 2000 minutes.
  • the thermal stability of the conventional hot-work steel B was low; the hardness difference in comparison with the alloy A according to the invention increased steadily up to 1000 minutes.

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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)
  • Forging (AREA)
  • Powder Metallurgy (AREA)
EP04450025.4A 2003-02-10 2004-02-10 Legierung und Gegenstand mit hoher Warmfestigkeit und hoher thermischer Stabilität Expired - Lifetime EP1445339B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
AT1962003A AT411905B (de) 2003-02-10 2003-02-10 Legierung und gegenstand mit hoher warmfestigkeit und hoher thermischer stabilität
AT1962003 2003-02-10

Publications (2)

Publication Number Publication Date
EP1445339A1 EP1445339A1 (de) 2004-08-11
EP1445339B1 true EP1445339B1 (de) 2016-08-03

Family

ID=29588323

Family Applications (1)

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EP04450025.4A Expired - Lifetime EP1445339B1 (de) 2003-02-10 2004-02-10 Legierung und Gegenstand mit hoher Warmfestigkeit und hoher thermischer Stabilität

Country Status (8)

Country Link
EP (1) EP1445339B1 (da)
AT (1) AT411905B (da)
BR (1) BRPI0400488B1 (da)
CA (1) CA2457183C (da)
DK (1) DK1445339T3 (da)
ES (1) ES2592714T3 (da)
HU (1) HUE030391T2 (da)
PT (1) PT1445339T (da)

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2904635B1 (fr) 2006-08-03 2008-10-31 Aubert & Duval Soc Par Actions Procede de fabrication d'ebauches en acier
FR2904634B1 (fr) 2006-08-03 2008-12-19 Aubert & Duval Soc Par Actions Procede de fabrication d'ebauches en acier
JP2010515824A (ja) * 2007-01-12 2010-05-13 ロバルマ，ソシエダッド アノニマ 優れた溶接性を有する冷間工具鋼
EP2083428A1 (fr) * 2008-01-22 2009-07-29 Imphy Alloys Alliage Fe-Co pour actionneur électromagnétique à grande dynamique

Family Cites Families (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB669396A (en) * 1938-12-06 1952-04-02 Boehler & Co Ag Geb Hot working tools and alloys therefor
US2715576A (en) * 1954-04-21 1955-08-16 Crucible Steel Co America Age hardening alloy steel of high hardenability and toughness
US3453152A (en) * 1963-11-12 1969-07-01 Republic Steel Corp High-strength alloy steel compositions and process of producing high strength steel including hot-cold working
US3453151A (en) 1965-03-09 1969-07-01 Park Chem Co Thermocouple with leak detector
JPH0765141B2 (ja) * 1985-09-18 1995-07-12 日立金属株式会社 熱間加工用工具鋼
JPH07228945A (ja) 1994-02-21 1995-08-29 Kobe Steel Ltd 耐食性に優れた高強度ばね用鋼
JP4232128B2 (ja) * 1998-08-03 2009-03-04 日立金属株式会社 被削性に優れた高強度プリハードン鋼材
JP2000119799A (ja) * 1998-10-07 2000-04-25 Hitachi Metals Ltd 耐食性を兼備した被削性および靱性に優れた高強度鋼材
KR100374980B1 (ko) * 1999-02-12 2003-03-06 히다찌긴조꾸가부시끼가이사 우수한 기계가공성을 갖는 다이스용 고장력강

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Publication number Publication date
BRPI0400488A (pt) 2005-07-12
ATA1962003A (de) 2003-12-15
CA2457183A1 (en) 2004-08-10
ES2592714T3 (es) 2016-12-01
HUE030391T2 (en) 2017-05-29
PT1445339T (pt) 2016-09-27
EP1445339A1 (de) 2004-08-11
BRPI0400488B1 (pt) 2014-04-15
AT411905B (de) 2004-07-26
CA2457183C (en) 2009-07-14
DK1445339T3 (da) 2016-09-26

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