EP1751321B1 - Acier a haute resistance mecanique et a l'usure - Google Patents

Acier a haute resistance mecanique et a l'usure Download PDF

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EP1751321B1
EP1751321B1 EP05770867.9A EP05770867A EP1751321B1 EP 1751321 B1 EP1751321 B1 EP 1751321B1 EP 05770867 A EP05770867 A EP 05770867A EP 1751321 B1 EP1751321 B1 EP 1751321B1
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Prior art keywords
steel
zirconium
titanium
optionally
content
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German (de)
English (en)
French (fr)
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EP1751321A2 (fr
Inventor
Jean Beguinot
Dominique Viale
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Industeel France SAS
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Industeel France SAS
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Priority to PL05770867T priority Critical patent/PL1751321T3/pl
Priority to SI200532254T priority patent/SI1751321T1/sl
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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
    • C22C38/18—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
    • C22C33/00—Making ferrous alloys
    • C22C33/006—Making ferrous alloys compositions used for making ferrous 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
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • 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
    • C22C38/42—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
    • C22C38/48—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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working

Definitions

  • the present invention relates to a steel with high mechanical strength and high wear resistance.
  • high wear resistance steels are used. Examples are steels intended to manufacture equipment for the mineral industries and which must resist abrasion. They are also steels intended to manufacture tools for cold or medium-hot forming of metal parts and which must withstand wear by metal-to-metal friction. For these tooling applications, at least the steels must retain good properties despite heating at temperatures up to 500 ° C or 600 ° C.
  • the steels considered here must have suitable properties in order to be machined or welded. They must finally be able to withstand shocks or intense efforts.
  • steels containing approximately between 0.3% and 1.5% of carbon, less than 2% of silicon and less than 2% of manganese are used. up to 3% nickel, between 1% and 12% chromium, between 0.5% and 5% molybdenum, with possible addition of vanadium or niobium.
  • the wear resistance results mainly from the hardening caused by the secondary precipitation of molybdenum carbides.
  • This resistance to wear can be improved, if necessary, by the presence of large léburitic carbides especially rich in chromium.
  • the object of the present invention is to remedy this drawback by proposing a means for obtaining a steel whose properties are equivalent to those known steels, but the harmfulness of segregated veins is significantly reduced.
  • the contents in W are preferably limited so that, after adjustment, W ⁇ 0.85% if Mo ⁇ 1.21% and W / Mo ⁇ 0.7 if Mo ⁇ 1.21%.
  • the steel may be such that: Ti + Zr / 2 ⁇ 0.7 ⁇ % to favor tenacity, or as: Ti + Zr / 2 ⁇ 0.7 ⁇ % in order to favor the resistance to wear.
  • the addition of titanium and / or zirconium is made by gradually adding titanium and / or zirconium to a slag covering the liquid steel bath and allowing the titanium and / or zirconium to slowly diffuse into the liquid steel bath.
  • titanium and / or zirconium can also be carried out by introducing a wire comprising titanium and / or zirconium into the bath of liquid steel, while stirring the bath.
  • the invention finally relates to a steel piece according to the invention that can be obtained by the manufacturing method according to the invention.
  • tungsten is an alloying element whose effects on the properties of steel are comparable to those of molybdenum.
  • tungsten has effects of hardening and resistance to thermal softening comparable to those of molybdenum in the proportion of two parts of tungsten to one part molybdenum.
  • tungsten is little used, except in some high-alloy steels not concerned by the present invention, and this, in particular, because it is much more expensive than molybdenum.
  • tungsten like molybdenum, has the disadvantage of segregating very strongly and giving rise to segregated veins very hard and very fragile.
  • the inventors have found, in a new and surprising way, that in the presence of sufficient quantities of titanium or zirconium, the segregation of tungsten is very substantially attenuated; effect particularly interesting to exploit when, in addition, the molybdenum content is already also relatively high.
  • This reduction applies to a steel, not according to the invention, which, before adjustment, contains mainly from 0.30% to 1.42% carbon, from 0.05% to 1.5% silicon, less than 1.95% manganese, less than 2.9% nickel, 1.1% to 7.9% chromium, 0.61% to 4.4% molybdenum, optionally up to 1.45% vanadium, up to 1.45% niobium, less than 1.45% tantalum with V + Nb / 2 + Ta / 4 ⁇ 1.45%.
  • This steel has a hardness index D, which will be explained later, between 800 and 1150.
  • It may contain, in addition, up to 0.1% of boron, up to 0.19% of sulfur, up to to 0.38% selenium, up to 0.79% tellurium, the sum S + Se / 2 + Te / 4 remaining less than 0.19%, optionally up to 0.01% calcium, up to at 0.5% rare earths, up to 1% aluminum and up to 1% copper.
  • All or part of the molybdenum is replaced by a substantially double proportion of tungsten, titanium and / or zirconium are added so as to obtain sufficient quantities of titanium and / or zirconium taking into account the amounts of tungsten introduced into the steel, and adjusting the carbon content so that, in particular, the hardness of the steel remains substantially unchanged.
  • the target composition for steel without tungsten so to obtain the desired job characteristics, in particular the level of hardness.
  • the target composition is then modified by choosing a tungsten content, thereby adjusting the molybdenum content and the titanium or zirconium and carbon contents, so that at least one of the main use characteristics, in particular the hardness, remains substantially unchanged.
  • a steel is developed corresponding to the modified analysis.
  • substantially unchanged is meant, for example, that the hardness of the steel after adjustment of the composition is equal to the hardness of the steel before adjustment of the composition to within 5%.
  • This tolerance is introduced to take into account the practical difficulties of producing a steel with precisely defined properties. However, it is desirable that the characteristics obtained are as close as possible to the characteristics targeted for the steel before adjustment of the composition. Also, it is preferable that the tolerance is only 2%, and, insofar as one is interested only in the targeted characteristics, it is still more preferable that the characteristic of hardness aimed after adjustment of the composition is equal to the characteristic of target hardness before adjustment of the composition.
  • the amount of tungsten added must be greater than or equal to 0.21%, preferably greater than 0.4%, more preferably greater than 0.7%, and more preferably greater than 1.05%. Indeed, the greater the substitution of molybdenum by tungsten, the greater the effect on segregations. However, this effect depends on the titanium or zirconium contents, which generally leads to further limiting the maximum addition of tungsten.
  • the titanium and zirconium contents must be such that the sum Ti + Zr / 2 is greater than or equal to 0.2 ⁇ W, preferably greater than or equal to 0.4 ⁇ W, more preferably greater than or equal to 0.6 x W.
  • the steel according to the invention contains at least 0.35% carbon, preferably more than 0.51%, and better still more than 0.65%, in order to form enough carbides and reach the level of hardness that it is desired to obtain, but up to 1.47% and preferably less than 1.1% and more preferably less than 0.98% in order to avoid too much embrittlement of the steel.
  • the steel contains titanium and zirconium, and these elements combine at high temperatures with carbon to form primary carbides.
  • the carbon called "free" which remains available to act on the properties of the matrix is free carbon, not combined with titanium and zirconium.
  • C * C - Ti / 4 - Zr / 8 (C, Ti and Zr being the contents of carbon steel, titanium and zinconium, respectively, in the following C will also be called “total carbon content”).
  • This quantity of available carbon must be sufficient to allow the precipitation of secondary carbides and in particular carbides of tungsten, molybdenum or other elements which are added to the steel, and from this point of view, this carbon content free C * must be greater than or equal to 0.3%. However, this content should not exceed 1.42%, and preferably 1.1% or better 0.98%, or more preferably 0.79%, not to excessively impair the toughness of the matrix itself.
  • the free carbon content C * remains less than 0.60% or even 0.50%.
  • Steel contains at least 0.05% silicon, as this element is a deoxidant. In addition, it contributes a bit to the hardening of steel. However, the silicon content must remain less than or equal to 1.5% and preferably less than or equal to 1.1%, better still 0.9%, and better still, less than or equal to 0.6%, in order to avoid excessively weaken the steel and too much reduce its ability to plastic deformation hot, for example by rolling. In addition, it may be desirable to impose a minimum silicon content of 0.45%, and better still 0.6%, in order to improve the machinability of the steel and also to improve the strength of the steel. oxidation.
  • the improvement in oxidation resistance is particularly desirable when the steel is used to manufacture workpieces intended to work at relatively high temperatures of the order of 450 ° C to 600 ° C, which requires resistance to oxidation. sufficient softening.
  • the content of Mo + W / 2 is desirable for the content of Mo + W / 2 to be greater than or equal to 2.2%.
  • the minimum values of silicon content, 0.45% or better still 0.6%, are more particularly advantageous when the contents of molybdenum and tungsten are such that the sum Mo + W / 2 is greater than or equal to 2 , 2%, without this nevertheless having an exclusive character.
  • the steel contains manganese up to 1.95% by weight in order to improve the hardenability of the steel, but this content should preferably remain less than or equal to 1.5% and better still less than or equal to 0, 9% to limit segregations that would lead to bad forgeability and insufficient toughness. It should be noted that the steel always contains a small amount of manganese, a few tenths of a percent, in particular to fix the sulfur and it is preferable that the Mn content is at least 0.4%.
  • Steel contains up to 2.9% nickel to adjust quenchability and improve toughness. But this element, is very expensive. Also, one does not generally seek a nickel content exceeding 0.9% or even 0.7%. Steel may not contain nickel but when nickel is not added voluntarily, it is interesting that steel contains up to 0.2% or even up to 0.4% in the form of residuals resulting from development.
  • the steel contains at least 1.1% chromium and better still more than 2.1%, and more preferably more than 3.1% and even more than 3.5%, to obtain sufficient quenchability and increase hardening to income, but up to 7.9%, and better still less than 5.9% or better still, less than 4.9% in order not to hinder the formation of secondary carbides, in particular containing Mo and / or W and, as such, more effective than the hardening chromium carbides.
  • this chromium content domain it is desirable to distinguish two preferred subdomains. Indeed, when the chromium content is sufficiently high, this element tends to form, especially in the segregated veins, type ledeburitic carbides that are coarse and more or less arranged in inter-dendritic networks. These carbides, despite a certain favorable effect on the wear resistance, contribute mainly to an embrittlement at least local matrix. So that when one wishes to privilege the hardness and the resistance to wear at the expense of toughness, it is desirable to choose a chromium content greater than or equal to 3.5%, favoring the presence of thedeburitic type carbides.
  • chromium content when seeking to promote the toughness of steel by accepting a slight reduction in wear resistance, it is preferable to choose a chromium content of less than or equal to 2.5%.
  • the molybdenum and tungsten contents of the steel must be such that the sum Mo + W / 2 is greater than or equal to 0.61%, preferably greater than or equal to 1.1%, and better still greater than or equal to 1, 6%. It is even desirable for this content to be greater than 2.2% in order to obtain a high degree of hardening and a better resistance to thermal softening, in particular when the use of the steel causes it to be heated up. at temperatures that may exceed about 450 ° C. This is the case, for example, of the steels used to produce mid-hot work tools for steel. In this case, the sum Mo + W / 2 can go up to 2.9%, even 3.4%, or even 3.9%, depending on the desired hardness and the temperature of income that one wishes to achieve on rooms. To achieve a very high level of resistance to wear of the matrix and minimize the effect of sap and thus delay the maximum removal of large carbides Ti and Zr, Mo + W / 2 can even go up to at 4.4%.
  • the tungsten content will be at least 0.21%, preferably at least 0.41%, better still at least 0.61%, in order to draw the best of the specific effect of tungsten.
  • the tungsten content depends on the desired degree of segregation deleteriousness reduction, as discussed above, and can also incorporate the cost of the alloy. This content may be up to 4.9% but will not usually exceed 1.9%; In general, content is lower than or equal to 0.90% or even 0.79%.
  • the molybdenum content may be at trace level, but preferably at least 0.51% and more preferably at least 1.4%; better still, at least 2.05%.
  • the tungsten content is limited to not more than 0.85% when the molybdenum content is less than 1.21%, and the tungsten / molybdenum ratio is limited to not more than 0.7 when the molybdenum content is greater than or equal to 1.21%.
  • titanium and zirconium must be adjusted so that the sum Ti + Zr / 2 is at least 0.21% and preferably greater than or equal to 0.41% or better, greater than or equal to 0, 61%, to obtain the desired effect of reducing the harmfulness of segregated veins.
  • these elements contribute to the formation of large carbides that improve wear resistance. However, this sum must remain less than 1.49% and preferably less than 1.19% or even less than 0.99% or even less than 0.79% so as not to deteriorate the toughness too much.
  • the titanium and zirconium contents must be adjusted according to whether it is desired to favor the tenacity of the steel or its resistance to wear.
  • the sum Ti + Zr / 2 should preferably remain below 0.7%.
  • the sum Ti + Zr / 2 must preferably be greater than or equal to 0.7%.
  • the titanium and zirconium contents must be sufficient with respect to the total carbon content C.
  • the product (Ti + Zr / 2) x C must be greater than or equal to 0.07, preferably greater than or equal to 0.12, and better still greater than or equal to 0.2.
  • the minimum titanium content may be 0%, or traces, but it is preferable that it be at least 0.21%, and better 0.41%, better still, 0.61%; the minimum zirconium content may be 0%, or traces, but it is preferable that it be at least 0.06%, or better still at least 0.11%.
  • the maximum content of titanium is 1.49% but can be reduced to 1.19%, or even 0.99%, better to 0.79% or even 0.7%, while the maximum content of Zirconium is 2.9%, preferably 0.9%, more preferably 0.49%.
  • the steel optionally contains up to 1.45% of vanadium, up to 1.45% of niobium, up to 1.45% of tantalum, the sum V + Nb / 2 + Ta / 4 being less than 1, 45%, better below 0.95% and even below 0.45%.
  • the minimum content is 0% or traces, but it is preferable that it be at least 0.11%, and more preferably at least 0.21%.
  • the level of addition of V + Nb / 2 + Ta / 4 helps to determine resistance and income response as indicated in the D index formulation.
  • Niobium although it can be used, has the disadvantage of precipitating at a higher temperature than vanadium, which greatly reduces the forgeability of the steel. Therefore the presence of niobium is not recommended and, in any case, it is desirable that the niobium content remains less than 1% or even 0.5% or, better still, less than 0.05%.
  • a sulfur content of less than 0.005% is preferable when looking for good toughness.
  • the steel optionally contains up to 0.5% rare earths to facilitate the germination of the carbides and refine the structure, and possibly up to 0.1% boron to improve the quenchability.
  • Steel can also contain up to 1% copper.
  • This element is not desired but can be provided by raw materials that would be too expensive to sort. Nevertheless, the copper content must be limited because this element has an adverse effect on hot ductility.
  • the presence of Ni in a content at least equal to that of copper is desired, at least when the copper content exceeds about 0.5%. Indeed, a sufficient content of nickel mitigates the harmfulness of copper.
  • the steel may contain aluminum which, like silicon, can contribute to the deoxidation of the liquid metal.
  • the aluminum content will be at trace level or better, at least equal to 0.006%, more preferably at least 0.020%.
  • the content of this element must remain less than or equal to 1% to ensure sufficient cleanliness, and preferably will not exceed 0.100%, better still less than 0.050%.
  • the rest of the composition consists of iron and impurities resulting from the elaboration. Note that, when an element is not added voluntarily during the elaboration, its content is 0% or traces, that is to say corresponding, depending on the element, either to the limits of detection by the methods of analysis are the quantities brought by the raw materials without there being a significant effect on the properties.
  • D is a hardness index which represents the hardening resulting from income for standard income conditions (550 ° C for 1 hour). The higher the value of D is, the higher the hardness after the temperature is determined at high temperature, or the higher the temperature that makes it possible to reach a given hardness level.
  • the hardness varies as a function of temperature and tempering time as is known to those skilled in the art.
  • the typical hardness levels obtained after returning to 550 ° C for one hour are, as an indication, respectively of the order of: 45HRC, 52 HRC, 57 HRC, 60 HRC and 63 HRC.
  • Group D 0.51 ⁇ % ⁇ C ⁇ 0.85 ⁇ % 0.21 ⁇ % ⁇ Ti ⁇ 0.70 ⁇ %
  • the hardness level can be adjusted by taking into account the influences of the various alloying elements indicated by the expression of the hardness index D.
  • the different groups in the order A, B, C, and D, are in the direction of a reinforcement of the level of toughness at the cost of a reduction in wear resistance.
  • titanium and zirconium it is desirable for titanium and zirconium to be in the form of primary carbides and not in the form of nitrides which are likely to form in the molten steel, especially when the transient overconcentrations of titanium and zirconium in the liquid just after the addition are too high given the levels of dissolved nitrogen that still exist in the liquid steel.
  • titanium and zirconium in such a way that these two elements react little with nitrogen and react essentially with carbon. This is achieved by avoiding, in the liquid phase of the steel, the transient over-concentrations of Ti or Zr during the additions of Ti and Zr.
  • a steel is poured in the form of a semi-finished product such as an ingot or a slab, it is shaped by hot plastic deformation and for example by rolling the semi-finished product, and then the product obtained is subjected to a possible heat treatment. .
  • the heat treatments to which the manufactured part can be subjected are of conventional type for tool steels.
  • Such a heat treatment may optionally comprise one or more anneals to facilitate cutting and machining, then austenitization followed by cooling in a mode adapted to the thickness, such as air or oil cooling. possibly followed by one or more income depending on the level of hardness you want to achieve.
  • the contents of molybdenum and tungsten in (Mos and Ws) and out (Moh and Wh) segregated veins were measured by means of a microprobe by masking the large titanium carbides in order to take into account the levels of Molybdenum and Tungsten in the matrix, apart from what can be fixed in these large carbides of titanium and zinconium (which are themselves likely to contain molybdenum or tungsten, forming in fact mixed carbides (Ti Zr Mo W) C ). In this way we appreciate the hardening and weakening part of Mo and W with respect to the metal matrix.
  • the examples a 1 , b 1 , c 1 and d 1 correspond to reference steels, that is to say steels whose composition is chosen before implementing the method according to the invention.
  • the other examples are deduced from these reference steels by the process according to the invention, except examples a 2 and b 2 for which the conditions relating to tungsten and titanium are not respected.
  • Example 1 is deduced from Example 1 by replacing 0.20% molybdenum with 0.40% tungsten, without adding titanium. It can be seen that the segregation rate is not significantly modified.
  • Example 3 is deduced from example a 1 not only by the replacement of 0.20% of molybdenum with 0.40% of tungsten, but also by the addition of 0, 40% titanium and the consequent adjustment of carbon. It is noted that the segregation rate of this steel is very significantly reduced compared with that of Examples 1 and 2 .
  • examples b 1 , b 2 and b 3 show that the addition of titanium and zirconium without addition of tungsten has no effect (comparison b1, b2), whereas the desired effect appears in the presence of tungsten partially substituted for molybdenum (comparison b2, b3).
  • Examples c 1 , c 2 and c 3 show that, with equal addition of tungsten, an increase in the addition of titanium has a favorable effect on the segregations.
  • examples 1 , 2 , and 3 show that an increase in the tungsten content has a favorable effect if the titanium or zirconium contents are sufficient.

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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)
  • Treatment Of Steel In Its Molten State (AREA)
  • Conductive Materials (AREA)
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EP05770867.9A 2004-05-21 2005-05-12 Acier a haute resistance mecanique et a l'usure Active EP1751321B1 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
PL05770867T PL1751321T3 (pl) 2004-05-21 2005-05-12 Stal o wysokiej wytrzymałości mechanicznej i odporności na zużycie
SI200532254T SI1751321T1 (sl) 2004-05-21 2005-05-12 Jeklo z visoko mehansko odpornostjo in odpornostjo proti obrabi

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR0405535A FR2870546B1 (fr) 2004-05-21 2004-05-21 Acier a haute resistance mecanique et a l'usure
PCT/FR2005/001191 WO2005123975A2 (fr) 2004-05-21 2005-05-12 Acier a haute resistance mecanique et a l'usure

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EP1751321A2 EP1751321A2 (fr) 2007-02-14
EP1751321B1 true EP1751321B1 (fr) 2019-03-06

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US (2) US7794651B2 (pt)
EP (1) EP1751321B1 (pt)
JP (1) JP5490991B2 (pt)
KR (2) KR20120126128A (pt)
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CA2565162A1 (fr) 2005-12-29
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FR2870546A1 (fr) 2005-11-25
US7794651B2 (en) 2010-09-14
KR20120126128A (ko) 2012-11-20
TWI371497B (en) 2012-09-01
WO2005123975A3 (fr) 2006-12-21
ZA200608963B (en) 2008-07-30
WO2005123975A2 (fr) 2005-12-29
FR2870546B1 (fr) 2006-09-01
CA2565162C (fr) 2013-07-30
AU2005254750B2 (en) 2009-10-29
US20080159901A1 (en) 2008-07-03
CN1957101A (zh) 2007-05-02
RU2006145432A (ru) 2008-06-27
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TW200600590A (en) 2006-01-01
AU2005254750A1 (en) 2005-12-29
JP5490991B2 (ja) 2014-05-14
US8097207B2 (en) 2012-01-17
KR20070017409A (ko) 2007-02-09
US20100221139A1 (en) 2010-09-02
SI1751321T1 (sl) 2019-07-31
ES2729644T3 (es) 2019-11-05
PL1751321T3 (pl) 2019-08-30
KR101214879B1 (ko) 2012-12-24
JP2007538154A (ja) 2007-12-27
BRPI0510826A (pt) 2007-11-27
BRPI0510826B1 (pt) 2017-09-26
TR201908207T4 (tr) 2019-06-21
HUE043693T2 (hu) 2019-09-30

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