EP1445339A1 - Alliage et article à haute résistance thermique et à haute stabilité thermique - Google Patents

Alliage et article à haute résistance thermique et à haute stabilité thermique Download PDF

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Publication number
EP1445339A1
EP1445339A1 EP04450025A EP04450025A EP1445339A1 EP 1445339 A1 EP1445339 A1 EP 1445339A1 EP 04450025 A EP04450025 A EP 04450025A EP 04450025 A EP04450025 A EP 04450025A EP 1445339 A1 EP1445339 A1 EP 1445339A1
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EP
European Patent Office
Prior art keywords
alloy
hardness
hot
molybdenum
high heat
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
EP04450025A
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German (de)
English (en)
Other versions
EP1445339B1 (fr
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
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Boehler Edelstahl GmbH
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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 with high hardness, high heat resistance and high thermal stability.
  • hot-work tool steels can be used as heat-treatable Iron-base alloys are called, whose increased mechanical Properties after the heat treatment, in particular their high strength and hardness up to temperatures of 500 ° C and above.
  • the hot hardness of such steels is given by a Elimination mechanism that is considered by the specialist as a secondary hardening increase wherein finest chromium-molybdenum-tungsten-vanadium carbides in Martensite grid are formed.
  • an alloyed material becomes one for the time being Solution heat treatment followed by increased cooling subjected to an alloying addition or phase completely or partially dissolved and kept in supersaturated solution.
  • One then heating to a temperature below the Solution annealing temperature causes a departure of the supersaturation of the (s) of the element (s) or the phase (s), which is a modification of Material properties, usually a material hardness increase causes.
  • 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 Kobait (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 enables the Property profile to improve a total of a manufactured article.
  • the object of the invention is a hot-work tool steel article at the same time high hardness and high toughness, high heat resistance and high to create thermal stability.
  • the object of the invention mentioned at the outset is with an alloy containing in% by weight: 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) below 1.3 Niobium (Nb) below 0.35 Iron (Fe) rest as well as accompanying elements and production-related contamination.
  • an iron-based alloy according to the invention is a carbon content of provided at least 0.15 wt .-%, so that one for a desired Secondary hardening increase sufficient amount of carbide is excreted.
  • higher Carbon concentrations as 0.44 wt .-% can with the provided carbide-forming elements form interfering primary toughening 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 Desoxidation due to at least 0.04 wt .-%, on the other hand but not higher than 0.3 wt .-%, because higher silicon values the Material toughness adversely affect.
  • Manganese is in a concentration between 0.06 and 0.4 wt .-% provided in the steel according to the invention. Lower levels can cause brittleness in a thermoforming and higher contents disadvantages for the hardenability of the Cause material.
  • Chromium contents below 1.2 wt .-% have an adverse effect on the Cured by the material, those of more than 5.0 wt .-% worsen the thermal stability of the same, because thereby the activity of molybdenum is pushed back.
  • the strong carbide former vanadium is according to the invention with a minimum content of 0.2 wt .-% provided sufficient, stable secondary curing of the Ensure steel. Higher contents than 0.8% by weight of vanadium especially at carbon contents in the upper region of the intended Concentration margin, leading to the excretion of primary carbides, causing the toughness properties of the material are abruptly deteriorated.
  • niobium Although the effect of niobium is similar to that of vanadium, it is remarkable through a formation of very stable carbides, so that the content of niobium should advantageously be less than 0.35 wt .-%.
  • 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.
  • Copper can form unwanted, intermetallic phases and should be less Concentration of less than 1.3 wt .-% be contained in the steel.
  • an alloy comprising one or more of the concomitant and 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 secondary hardening superimposed by carbides may be advantageous when the value nickel content refracted by aluminum content in each case in wt .-% between 1.8 and 4.2, preferably between 2.1 and 3.9. This will be a Overhang of a precipitate forming element avoided.
  • the stated object of the invention is according to an improved Property profiles solved with a hot work tool object, if one after produced by a fusion metallurgy or powder metallurgy process Starting material, in particular by hot forming and machining in the form which molded article after a curing Heat treatment secondary precipitated carbides, as well as intermetallic Has precipitates.
  • the total hardness of the material is advantageous by an overlay the secondary hardness increase by carbide precipitations and the Elimination hardening achieved.
  • high material hardness values can be achieved
  • the tempering technology is based on maintaining high material toughness is directed and compared with a hot work tool according to the state of Technique use lower hardening temperatures.
  • This lower one Austenitizing temperature can also provide significant advantages in terms of a low distortion in a tempering treatment of complicated shaped parts to have.
  • the toughness is particularly high at high hardness values and thermal stability up to 50 ° C and more to higher temperatures postponed.
  • a hot-work tool according to the invention which has secondarily precipitated chromium-molybdenum-vanadium mixed carbides and essentially intermetallic phases of the Al Fe 2 Ni type in the microstructure, has a particularly preferred property profile and can be economically produced in conventional hardening plants at comparatively low hardening temperatures ,
  • a pronounced thermal stability of the object can be achieved if the alloy has a ratio of chromium + molybdenum + vanadium broken by carbon, in each case in wt .-% of greater than 13, but less than 19 has.
  • 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 conventional hot-work steel B, a maximum hardness value of 56 HRC at 500 ° C.
  • a hardness determination on the test specimen at the test temperature was carried out after the Rebound hardness method (Shore hardness) is performed, for which return values So far only a conversion into Vickers hardness values is available.

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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 Alliage et article à haute résistance thermique et à haute stabilité thermique Expired - Lifetime EP1445339B1 (fr)

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 true EP1445339A1 (fr) 2004-08-11
EP1445339B1 EP1445339B1 (fr) 2016-08-03

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Family Applications (1)

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EP04450025.4A Expired - Lifetime EP1445339B1 (fr) 2003-02-10 2004-02-10 Alliage et article à haute résistance thermique et à haute stabilité thermique

Country Status (8)

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

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2008015260A1 (fr) * 2006-08-03 2008-02-07 Aubert & Duval Procédé de transformation d'ébauches d'acier
WO2008084108A1 (fr) * 2007-01-12 2008-07-17 Rovalma Sa Acier pour outil d'estampage à froid présentant une remarquable soudabilité
US8101004B2 (en) 2006-08-03 2012-01-24 Aubert & Duval Process for manufacturing steel blanks

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2083428A1 (fr) * 2008-01-22 2009-07-29 Imphy Alloys Alliage Fe-Co pour actionneur électromagnétique à grande dynamique

Citations (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
US3453151A (en) 1965-03-09 1969-07-01 Park Chem Co Thermocouple with leak detector
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
US4729872A (en) * 1985-09-18 1988-03-08 Hitachi Metals, Ltd. Isotropic tool steel
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
JP2000054068A (ja) * 1998-08-03 2000-02-22 Hitachi Metals Ltd 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
EP1036852A1 (fr) * 1999-02-12 2000-09-20 Hitachi Metals, Ltd. Acier à haute résistance mécanique pour estampes à usinabilité excellente

Patent Citations (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
US4729872A (en) * 1985-09-18 1988-03-08 Hitachi Metals, Ltd. Isotropic tool steel
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
JP2000054068A (ja) * 1998-08-03 2000-02-22 Hitachi Metals Ltd 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
EP1036852A1 (fr) * 1999-02-12 2000-09-20 Hitachi Metals, Ltd. Acier à haute résistance mécanique pour estampes à usinabilité excellente

Non-Patent Citations (3)

* Cited by examiner, † Cited by third party
Title
PATENT ABSTRACTS OF JAPAN vol. 1995, no. 11 26 December 1995 (1995-12-26) *
PATENT ABSTRACTS OF JAPAN vol. 2000, no. 05 14 September 2000 (2000-09-14) *
PATENT ABSTRACTS OF JAPAN vol. 2000, no. 07 29 September 2000 (2000-09-29) *

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2008015260A1 (fr) * 2006-08-03 2008-02-07 Aubert & Duval Procédé de transformation d'ébauches d'acier
FR2904635A1 (fr) * 2006-08-03 2008-02-08 Aubert & Duval Soc Par Actions Procede de fabrication d'ebauches en acier
US8101004B2 (en) 2006-08-03 2012-01-24 Aubert & Duval Process for manufacturing steel blanks
US8252129B2 (en) 2006-08-03 2012-08-28 Aubert & Duval Method for transforming steel blanks
US8551397B2 (en) 2006-08-03 2013-10-08 Aubert & Duval Process for manufacturing steel blanks
CN101553590B (zh) * 2006-08-03 2014-08-06 奥贝尔&杜瓦尔公司 钢坯的变形方法
WO2008084108A1 (fr) * 2007-01-12 2008-07-17 Rovalma Sa Acier pour outil d'estampage à froid présentant une remarquable soudabilité
US9249485B2 (en) 2007-01-12 2016-02-02 Rovalma Sa Cold work tool steel with outstanding weldability

Also Published As

Publication number Publication date
HUE030391T2 (en) 2017-05-29
BRPI0400488A (pt) 2005-07-12
AT411905B (de) 2004-07-26
DK1445339T3 (en) 2016-09-26
PT1445339T (pt) 2016-09-27
EP1445339B1 (fr) 2016-08-03
ATA1962003A (de) 2003-12-15
CA2457183C (fr) 2009-07-14
ES2592714T3 (es) 2016-12-01
CA2457183A1 (fr) 2004-08-10
BRPI0400488B1 (pt) 2014-04-15

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