EP0499298B1 - Ausscheidungshärtbarer, austenitischer Warmarbeitsstahl und Verfahren zur Behandlung desselben - Google Patents

Ausscheidungshärtbarer, austenitischer Warmarbeitsstahl und Verfahren zur Behandlung desselben Download PDF

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Publication number
EP0499298B1
EP0499298B1 EP92200085A EP92200085A EP0499298B1 EP 0499298 B1 EP0499298 B1 EP 0499298B1 EP 92200085 A EP92200085 A EP 92200085A EP 92200085 A EP92200085 A EP 92200085A EP 0499298 B1 EP0499298 B1 EP 0499298B1
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EP
European Patent Office
Prior art keywords
steel
hot
max
steel according
precipitation
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Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Expired - Lifetime
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EP92200085A
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English (en)
French (fr)
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EP0499298A1 (de
Inventor
Lars-Ake NORSTRÖM
Odd Sandberg
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Uddeholms AB
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Uddeholms AB
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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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese

Definitions

  • the present invention relates to a precipitation hardenable, austenitic hot work steel having a high hot yield strength, a good resistance to tempering as well as good hot ductility (toughness) at temperatures of about 700°C.
  • the invention also relates to a method of treating such a steel.
  • the molding tools are subjected to very high temperatures as well as to a high mechanical load.
  • the blanks to be formed generally are preheated to temperatures of above 700°C, and thus, the working tool surface in contact with the work piece may reach temperatures of about 700°C.
  • the tool life ordinarily is limited by the development of any of the following damages, resulting in a rejection of the tool:
  • martensitic hot work steels e.g. type AISI H13 (about 0.40% C-1.0% Si-0.5% Mn-5% Cr- 1.3% Mo-0.9% V). These steel grades have a good ductility/toughness but unfortunately an insufficient hot strength and resistance to tempering at the temperatures of interest (about 700°C). Consequently, their tool lives ordinarily are too short as regards primarily hot wearing and plastic deformation, respectively.
  • so called superalloys are used increasingly, which are highly alloyed metallic materials, usually precipitation hardened by means of intermetallic phases. Such materials may have a very high hot strength and resistance to tempering-back and have very satisfactory tool lives in many instances.
  • the drawbacks of the superalloys are that they are very expensive to use due to their chemical composition and difficult to obtain (difficult to manufacture) in sufficiently large dimensions.
  • superalloys used in this connection, are e.g.: iron base ally A 286 (about 0.04% C-15% Cr- 26% Ni- 1.3% Mo-2.0% Ti-0.2% Al) and nickel base alloy René 41 (about 0.10% C- 19% Cr-55% Ni-11% Co-10% Mo- 3% Ti-1.5% Al), respectively.
  • Ceramic materials are being used increasingly for smaller tools in this field. Ceramic materials can have an extremely good hot strength and resistance to tempering-back. However, the problem with the ceramic materials available so far is that they are too brittle and thus, they too easily cause tool breakdowns due to crack formation/ruptures. Also, they are very expensive and it is difficult to machine them, thus causing very high tool costs.
  • GB-A-1 384 234 discloses a hot work tool steel made from an austenitic steel alloy hardened by carbide precipitation.
  • the alloy comprises 0.62 %C, 19.1 %Mn, 4.33 %Cr, 1.8 %V, 0.81 %Mo, 0,95 Si and 0.11 %Ni.
  • the object of the present invention is to suggest a steel material for tools, used to hot form copper, brass and steel, having the following combination of properties:
  • Steel materials having the above-mentioned characteristics are according to the invention precipitation hardenable, austenitic alloys with the following composition ranges (percent by weight): 0.35-0.60 C max. 1 Si 9-17 Mn 2-8 Cr max. 2 Ni 1-4 Mo, which completely or partially can be replaced by the double amount of W (percent by weight) 1.2-1.8 V 0.001-0.020 B The remainder essentially Fe and impurities.
  • Carbon and vanadium in combination constitute the main ingredient of the precipitation hardening phase vanadium carbide (MC).
  • the effect of the precipitation hardening is dependent on the amount of carbon and vanadium present in solution after the solution heat treatment. At least about 0.35, preferably at least 0.4% carbon is needed in order to obtain an efficient hardeing effect. However, it is not possible to dissolve more than about 0.6% carbon, when this type of steel is solution heat treated. Surplus carbon remains in the form of not dissolved vanadium carbides, which impairs the ductility/toughness of the steel in a not desirable way. This means, that the steel according to the invention is to contain 0.35 - 0.60% carbon, with an optimal carbon content in the range 0.4-0.5% carbon.
  • Silicon is not a necessary alloy element according to the invention, but it can be used in amounts, which are normal, when deoxidization is used in steel making. However, silicon stimulates the carbon activity in austenite, which means that silicon counteracts the necessary solution of vanadium carbide during the solution heat treatment. Therefore the silicon content is limited according to the invention to a maximum of 1%.
  • Manganese is a strongly austenite stabilizing element and is used according to the invention in order to make the steel austenitic at all temperatures. We have found that at least about 9% Mn, preferably at least 10% Mn is necessaryy in order to obtain this. Also, manganese lowers the carbon activity in the austenite and consequently improves at the same time the solution of vanadium carbide during the solution heat treatment. However, a high manganese content leads to certain metallurgical complications in the steel making and thus, a too high content means unnecessary problems and costs. Thus, the manganese content is limited to not more than 17%, preferably not more than 15%, with an optimal manganese content in the range 10.5-13%.
  • Chromium arid manganese have similar effects on the austenite stabilizaion and the carbon activity. Also, chromium improves in a desirable way the oxidation resistance of the steel. Thus, at least 2% chromium, preferably at least 3% chromium ought to be added to the steel. However, when a chromium content more than about 10% is used, chromium starts forming chromium carbides to a not desirable degree during the ageing treatment, which has a detrimental effect on the precipitation hardening from vanadium carbides. Consequently, the steel according to the invention suitably must not contain more than 8% chromium, preferably not more than 7% chromium, with an optimal chromium content in the range 4-6% chromium.
  • Nickel is like manganese a strongly austenite stabilizing element and consequently, it can partly replace manganese in the steel.
  • nickel stimulates the carbon acitvity of the austenite in a way which impairs the solution treatment. Therefore, nickel is not a desirable alloy element in this respect and the nickel content is limited according to the invention to not more than 2%, preferably not more than 0.5%.
  • the steel ought to contain nickel only in amounts, which are normal for unavoidable accessory elements.
  • Molybdenum improves the resistance to tempering-back of the steel by delaying the coarsening of the vanadium carbides during an over-ageing. Also, molybdenum results in substantial increases in the hot yield strength, partly due to a solution hardening contribution. Consequently, molybdenum ought to be used in an amount not less than 1%. The effect of molybdenum increases, when the amount increases up to about 4%, where a saturation tendency appears. Therefore, molybdenum should be used in an amount of between 1 and 4%, with an optimal content in the range 2-3%.
  • tungsten and molybdenum are very similar, even if the atomic weight of tungsten is twice as large as that of molybdenum, it is reasonable to expect, that similar effects can be obtained with a tungsten addition, in an amount which is twice as large, expressed in weight-percentage. Consequently, it may be possible to replace, fully or partially, molybdenum with tungsten in an amount, which is twice as large, expressed in weight-percentage.
  • molybdenum should not be replaced by tungsten at all in the steel, and therefore, the preferred composition of the steel contains tungsten only at impurity levels.
  • Vanadium is the main ingredient in the precipitation hardened phase vanadium carbide (MC). Consequently, this substance is a key element according to the invention and when the present carbon contents are used, at least about 1.2% vanadium is required in order to obtain a reasonably efficient hardening effect. However, too high a vanadium content impairs the necessary solution of the vanadium carbide during the solution treatment, and therefore, the steel should not contain more than 1.8% vanadium. The optimal vanadium content is found in the range 1.3-1.7%.
  • the weak link of the microstructure as regards the ductility/toughness of a precipitation hardened, austenitic steel of this type is the strength (cohesion) of the austenite grain boundaries.
  • the grain boundaries are usually weaker than the interior of the grains and consequently, the ruptures tend to follow the grain boundaries, resulting in a low ductility/toughness.
  • This situation primarily depends on the precipitation of unfavorable grain boundary carbides (e.g. M23C6, in which M is Cr, Mo, Mn and Fe) during the ageing, in combination with the desirable finely dispersed intragranular vanadium carbide. These grain boundary carbides make the grain boundaries brittle by lowering their cohesion.
  • boron is of crucial importance as a microalloy ingredient.
  • it will end up mainly in the austenite grain boundaries thanks to its very low solubility in the steel.
  • boron dramatically alters the conditions in the grain boundaries and then also the conditions for a precipitation of grain boundary carbides.
  • this type of steel boron additions apparently lower the amount of obtained grain boundary carbides as well as their capacity to make the steel brittle in a way, which is very important to the hot ductility/toughness (a doubling of the coefficient of cross-sectional contraction in a tensile testing machine at 700°C).
  • the steel according to the invention shall contain at least 0.001% boron, but in order to obtain the desired effect without doubt the amount of boron ought to be at least 0.003%.
  • too high amounts of boron may result in easily fusible boride phases, which is disadvantageous as regards the processing (forging/milling) of the steel.
  • the amount of boron ought to be not more than 0.020%, preferably not more than 0.015%.
  • Castings made of steel No. 6 were forged and milled under conditions similar to production conditions, the results being excellent, to various rod dimensions of between 30 mm ⁇ and 150 mm ⁇ . This shows clearly that this steel can be made using conventional steel production methods within a dimensional area, which is suitable for the intended use.
  • the obtained results show that the steel according to the invention has a very attractive combination of high temperature strength, resistance to tempering-back and hot ductility (toughness).

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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)
  • Coating With Molten Metal (AREA)
  • Heat Treatment Of Articles (AREA)

Claims (10)

  1. Aushärtbarer, austenitischer Warmarbeitsstahl, der eine hohe Warmstreckfestigkeit, eine gute Beständigkeit gegen Anlassen und eine gute Warmdehnbarkeit (Zähigkeit) bei Temperaturen von etwa 700°C aufweist, dadurch gekennzeichnet, daß er die folgende Zusammensetzung, ausgedruckt in Gew.-%, aufweist:
    0,35 - 0,60 C
    max. 1 Si
    9 - 17 Mn
    2 - 8 Cr
    max. 2 Ni
    1 - 4 Mo, das ganz oder teilweise gegen die doppelte Menge an W (Gew.-%) ausgetauscht sein kann
    1,2 - 1,8 V
    0,001 - 0,020 B
    der Rest Eisen und Verunreinigungen in normalen Mengen.
  2. Stahl gemäß Anspruch 1, dadurch gekennzeichnet, daß er 0,4 - 0,5 C enthält.
  3. Stahl gemäß Anspruch 1, dadurch gekennzeichnet, daß er 10 - 15 Mn enthält.
  4. Stahl gemäß Anspruch 3, dadurch gekennzeichnet, daß er 10,5 - 13 Mn enthält.
  5. Stahl gemäß Anspruch 1, dadurch gekennzeichnet, daß er 3 - 7 Cr, vorzugsweise 4 - 6 Cr, enthält.
  6. Stahl gemäß Anspruch 1, dadurch gekennzeichnet, daß er 2 - 3 Mo enthält.
  7. Stahl gemäß Anspruch 1, dadurch gekennzeichnet, daß er 1,3 - 1,7 V enthält.
  8. Stahl gemäß Anspruch 1, dadurch gekennzeichnet, daß er 0,003 - 0,015 B enthält.
  9. Stahl gemäß einem der Ansprüche 1 - 8, dadurch gekennzeichnet, daß er die folgende chemische Zusammensetzung aufweist:
    0,42 - 0,48 C
    0,1 - 0,8 Si
    11,6 - 12,4 Mn
    4,5 - 5,5 Cr
    max. 0,5 Ni
    2,2 - 2,8 Mo
    1,2 - 1,6 V
    0,003 - 0,015 B
    der Rest Eisen und Verunreinigungen.
  10. Verfahren zur Behandlung eines Stahls, der die folgende chemische Zusammensetzung, ausgedrückt in Gew.-%, aufweist:
    0,35 - 0,60 C
    max. 1 Si
    9 - 17 Mn
    2 - 8 Cr
    max. 2 Ni
    1 - 4 Mo, das ganz oder teilweise gegen die doppelte W-Menge (Gew.-%) ausgetauscht sein kann
    1,2 - 1,8 V
    0,001 - 0,020 B
    der Rest Eisen und Verunreinigungen in normalen Mengen, und zur Herstellung von Werkzeugen aus diesem Stahl, dadurch gekennzeichnet, daß der Stahl zu Stäben oder Blöcken geschmiedet und/oder warm gewalzt wird, wobei der Borgehalt des Stahls vorzugsweise in den Austenit-Korngrenzen vorkommt, in denen die Gegenwart von Bor der Ausscheidung von für die Dehnbarkeit ungünstigen Korngrenzen-Carbiden entgegenwirkt, daß der geschmiedete und/oder warm gewalzte Stahl im Temperaturbereich 1100 - 1200°C lösungsbehandelt und auf Umgebungstemperatur abgegekühlt wird, wobei der Stahl eine austenitische Matrix behält und eine Härte von max. 30 HRC erhält, daß aus diesem lösungsbehandelten Stahl durch Schneidformung Werkzeuge in einem mindestens nahezu fertigen Zustand hergestellt werden und daß die Werkzeuge im Temperaturbereich 650 - 750°C vergütungsbehandelt werden, wobei eine sehr fein dispergierte und temperaturbeständige, intragranulare Ausscheidung von Vanadiumcarbid (MC) in der noch immer austenitischen Matrix erhalten wird und eine Härte wegen der Aushärtung auf mehr als 40 HRC zunimmt.
EP92200085A 1991-02-13 1992-01-14 Ausscheidungshärtbarer, austenitischer Warmarbeitsstahl und Verfahren zur Behandlung desselben Expired - Lifetime EP0499298B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
SE9100424 1991-02-13
SE9100424A SE467929B (sv) 1991-02-13 1991-02-13 Utskiljningshaerdande, austenitiskt varmarbetsstaal samt saett att framstaella verktyg av staalet

Publications (2)

Publication Number Publication Date
EP0499298A1 EP0499298A1 (de) 1992-08-19
EP0499298B1 true EP0499298B1 (de) 1995-04-12

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EP92200085A Expired - Lifetime EP0499298B1 (de) 1991-02-13 1992-01-14 Ausscheidungshärtbarer, austenitischer Warmarbeitsstahl und Verfahren zur Behandlung desselben

Country Status (7)

Country Link
EP (1) EP0499298B1 (de)
JP (1) JPH0578786A (de)
AT (1) ATE121141T1 (de)
CA (1) CA2059853A1 (de)
DE (1) DE69201981T2 (de)
ES (1) ES2072080T3 (de)
SE (1) SE467929B (de)

Families Citing this family (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
AU707536B2 (en) * 1996-02-16 1999-07-15 Australian Wool Research & Promotion Organisation Improvements in shearing combs and cutters
CN100343406C (zh) * 2005-10-08 2007-10-17 四川大学 一种微米晶铁基形状记忆合金块材的制备方法
DE102007046410A1 (de) * 2007-09-24 2009-04-02 Volkswagen Ag Gießereiwerkzeug und Verfahren zur Herstellung eines solchen Werkzeuges sowie dessen Verwendung
DE102008005803A1 (de) * 2008-01-17 2009-07-23 Technische Universität Bergakademie Freiberg Bauteil aus höher kohlnstoffhaltigem austenitischem Stahlformguss, Verfahren zu deren Herstellung und deren Verwendung
CN104213044B (zh) * 2014-08-26 2016-04-06 清华大学 一种铜合金压铸模具钢及其制备方法
EP3735479A4 (de) 2018-01-05 2021-07-28 The University of Hong Kong Automobilstahl und verfahren zur herstellung davon
CN113549832A (zh) * 2021-07-20 2021-10-26 苏州雷格姆海洋石油设备科技有限公司 高压氢能装备用a286高强高温合金锻件的生产工艺

Family Cites Families (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE1032296B (de) * 1952-08-22 1958-06-19 East Hecla Works Verwendung einer austenitischen Stahllegierung als Werkstoff fuer nichtmagnetische Gegenstaende hoher Festigkeit und Streckgrenze
SE343892B (de) * 1969-02-10 1972-03-20 Bofors Ab
GB1384234A (en) * 1971-01-28 1975-02-19 Dunford Hadfields Ltd Hot work tools made from steel alloys
GB1310183A (en) * 1971-04-20 1973-03-14 Prvni Brnenska Strojirna Austenitic steel alloys

Also Published As

Publication number Publication date
JPH0578786A (ja) 1993-03-30
SE467929B (sv) 1992-10-05
DE69201981T2 (de) 1995-08-24
ATE121141T1 (de) 1995-04-15
DE69201981D1 (de) 1995-05-18
CA2059853A1 (en) 1992-08-14
ES2072080T3 (es) 1995-07-01
SE9100424L (sv) 1992-08-14
SE9100424D0 (sv) 1991-02-13
EP0499298A1 (de) 1992-08-19

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