WO2003069009A1 - Materiau d'acier contenant des carbures et utilisation du materiau - Google Patents

Materiau d'acier contenant des carbures et utilisation du materiau Download PDF

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Publication number
WO2003069009A1
WO2003069009A1 PCT/SE2003/000224 SE0300224W WO03069009A1 WO 2003069009 A1 WO2003069009 A1 WO 2003069009A1 SE 0300224 W SE0300224 W SE 0300224W WO 03069009 A1 WO03069009 A1 WO 03069009A1
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Prior art keywords
steel material
material according
max
steel
carbides
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PCT/SE2003/000224
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English (en)
Inventor
Odd Sandberg
Roger Andersson
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Uddeholm Tooling Aktiebolag
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Priority to AU2003206341A priority Critical patent/AU2003206341A1/en
Publication of WO2003069009A1 publication Critical patent/WO2003069009A1/fr

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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
    • C22C38/001—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
    • C22C38/02—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/30—Ferrous alloys, e.g. steel alloys containing chromium 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

Definitions

  • the invention relates to a steel material intended to be used for construction elements in environments which require a good corrosion resistance.
  • the invention concerns a steel material which also has a good abrasive wear resistance in the hardened and the tempered condition of the steel.
  • the invention also concerns the use of the steel material for construction elements, particularly fixtures or fixture details for workpieces to be machined in eroding machines, such as spark machining machines, in the liquid bath of which the fixture or the fixture details are subjected to abrasive wear.
  • Mould steels for plastic moulding tools and holder steels for plastic moulding tools are other conceivable applications.
  • the machining of the engraving i.e. the mould cavity of mould tools, to a large extent is performed in a water bath in eroding machines, such as spark machining machines.
  • the water bath can gradually become very corrosive because of the electrochemical currents which are generated in the bath.
  • metal fragments of the workpiece can be released and form a slurry in the water bath which therefore also becomes strongly abrasive.
  • the workpiece is secured by means of fixtures, the details of which are repeatedly used. They are therefore subjected to prolonged influence by the corrosive and abrasive environment in the water bath.
  • the mould steel When engineering plastics are moulded, the mould steel is subjected to high tensions and wear as well as corrosion. Therefore high hardness, good wear resistance, corrosion resistance and sufficient ductility are important features of the mould steel. Also the holders for the plastic mould tools are subjected to similar stresses, for which reason also the holder material should possess the above mentioned product features.
  • the nominal compositions of the said steels in weight-% are given in Table 1. Besides the elements mentioned in the table, the steels contain iron and normally occurring impurities and accessory elements.
  • RIGOR ® is a steel having a good wear resistance but insufficient corrosion resistance.
  • STAVAX ® has a comparatively good wear resistance, however not sufficient.
  • the corrosion resistance is good for the fields of use which are interesting.
  • RAMAX ® has a corrosion resistance which is sufficiently good for the field of use for that steel, but has an insufficient wear resistance.
  • ELMAX ® has a good corrosion resistance and a good wear resistance, but not a sufficiently good machineability. It also requires a powder metallurgy manufacturing and may therefore be said to be too exclusive and too qualified to be defined as a volume product for fixture materials.
  • the steel material thus in the first place shall satisfy some or all of the following criteria: • Excellent corrosion resistance, particularly good resistance against pitting when the material is used for fixtures or fixture details submerged in a bath in an eroding machine, such as a spark machining machine, as well as when the material is used for moulds for plastic moulding and for holders for mould tools for plastic moulding. • Sufficient wear resistance for the said applications, e.g. a wear resistance which is comparable with that of steels of type RIGOR ® .
  • Carbon shall be present to a sufficient amount in the steel in order to be able to form, together with nitrogen and carbide and nitride formers existing in the steel, in the hardened and tempered condition of the steel, 3-12 vol-% carbides, nitrides and/or carbonitrides, including 2-10 vol-% M C 3 -carbides, nitrides and/or carbonitrides, where M mainly is chromium, and 0.1-2.0 vol-%, preferably at least 0.3 vol% MC-carbides, nitrides and/or carbonitrides, where M mainly is vanadium, in a matrix which essentially consists of tempered martensite.
  • the total amount of carbon in the steel i.e.
  • the carbon that is dissolved in a matrix of the steel and the carbon which is bound in carbides shall be at least 0.5 %, preferably at least 0.6 %, suitably at least 0.7 %, while the maximal content of carbon may amount to 1.3 %, preferably max. 1.14 %, suitably max. 1.0 %.
  • the most preferred carbon range depends on the specific application of the steel, which in the first place is fixtures and fixture details and moulds for plastic moulding and holders for mould assemblies, respectively, as above mentioned, and the specific application in turn, according to an aspect of the invention, should have great importance when the most suitable chromium content is selected. Therefore, as far as the most preferred carbon content range is concerned, reference is made to the below discussion in connection with the chromium content of the steel.
  • nitrogen exists as an unavoidable element because the manufacturing of the steel comprises spray forming using nitrogen as an atomising gas.
  • the steel thus contains max. 0.15 N, typically 0.06-0.12 % N. It is also conceivable, according to an embodiment of the invention, to increase the nitrogen content to at least 0.3 %, preferably at least 0.8 %, by means of any known technique, i.e. by pressurising the steel melt in a nitrogen gas atmosphere, addition of chromium nitride to the melt under advanced pressure, or by any other mode. When nitrogen exists in the mentioned amounts, nitrogen is not a harmful ingredient.
  • nitrogen may have a favourable effect by forming vanadium- and chromium- carbonitrides together with carbon. Therefore, also a minor fraction of carbonitrides may be included in the above mentioned volume contents of MC- and M C 3 -carbides. Also powder metallurgy manufacturing of the steel in principle is conceivable, which could include gas atomising of a metal melt using nitrogen as an atomising gas, but that technique also requires hot isostatic compaction and is expensive, which makes it difficult or impossible to satisfy the requirement as far as a good manufacturing economy is concerned.
  • Silicon exists as a residue from the manufacturing of the steel and exists in an amount of at least 0.1 %. Silicon increases the carbon activity in the steel and can therefore contribute to the provision of an adequate hardness of the steel without creating embrittlement problems.
  • the steel therefore contains at least 0.15 % and suitably at least 0.3 % Si. Silicon, however, is a strong ferrite former and must therefore not exist in amounts exceeding 1.5 %.
  • the steel does not contain more than 1.0 %, preferably max. 0.8 % Si. The nominal silicon content is about 0.5 %.
  • Manganese is also present as a residual from the manufacturing of the steel and binds the amounts of sulphur which may exist in low contents in the steel, by the formation of manganese sulphide. Manganese therefore exists in an amount of at least 0.1 %.
  • Manganese also promotes the hardenability, which is favourable. Manganese, however, must not exist in amounts above 1.5 % in order to avoid embrittlement problems.
  • the steel does not contain more than max. 1.0 %, preferably max. 0.6 % Mn.
  • the content of manganese is in the range 0.2-0.5 % Mn.
  • the nominal manganese content is 0.30 %.
  • Chromium shall exist in an amount of at least 14 %, preferably in an amount of at least 14.5 %, suitably at least 15.0 % in order to afford the steel a desirable corrosion resistance. Chromium also is an important carbide- and nitride former and forms, together with carbon and existing nitrogen M7C3 -carbides, -nitrides, and/or -carbonitrides, which together with the MC-carbides, -nitrides, and/or -carbonitrides, contribute to the desired wear resistance. Chromium, however, is a strong ferrite former. In order to avoid ferrite after hardening from 1000-1150°C, the chromium content must not exceed 19 %, preferably not exceed max. 18.0 %, suitably max. 17.0 %.
  • the most preferred carbon- and chromium contents are related to the specific use of the steel.
  • initial experiments indicated that the most preferred range of carbon content is 14-15 % Cr and that the most preferred range of the carbon content is 0.55-0.75 % C.
  • the nominal content for that application therefore should be 14.5 % Cr, and 0.65 % C, respectively.
  • mould steels for mould tools for moulding plastic materials and holders for such tools the initial experiments indicated that the most preferred content ranges should be 16-17 % Cr and 0.8-1.0 % C, respectively.
  • the nominal contents in that case should be 16.5 % Cr and 0.9 % C, respectively. Later experiments, however, have modified the most preferred ranges for said application to 14.8-16.0 % Cr, nominally 15.6 % Cr, and 0.80-0.90 % C, nominally 0.85 % C, respectively, at the same time as the nitrogen content should rest in the range 0.06-0.12 % N, nominally at about 0.09 % N.
  • Nickel is an optional element and may as such optionally exist as an austenite stabilising element in an amount of max. 2.0 %, preferably max. 1.0 %, suitably max. 0.7 %, in order to balance the high contents in the steel of chromium and molybdenum, which are ferrite forming elements.
  • the steel according to the invention does not contain any intentionally added amount of nickel.
  • Nickel may be tolerated as an unavoidable impurity, which as such may be as high as about 0.3 or 0.4 %.
  • Cobalt also is an optional element and may as such optionally exist in an amount of max. 2.0 %, preferably max. 0.7 %, in order to further improve the tempering resistance. Normally, however, no addition of cobalt is required in order to achieve the desired properties of the steel. Suitably, the steel therefore does not contain any intentionally added cobalt, which however may exist as an impurity in an amount up to 0.1 %, emanating from used raw materials for the manufacturing of the steel.
  • Molybdenum shall exist in an amount of at least 1.0 % in order to afford the steel a desired corrosion resistance, particularly a good pitting corrosion resistance, as well as a good hardenability. Molybdenum also is a valuable carbide former and should therefore exist in the steel in an amount exceeding said content of at least 1.0 %, which is required from reasons which have to do with corrosion resistance. In principle, however, molybdenum in its capacity as carbide former may be replaced by twice the amount of tungsten.
  • the content of the steel of Mo + W/2 shall amount to at least 1.5 %, preferably at least 1.8 % and suitably at least 2.0 % in order on one hand to afford the steel a desired corrosion resistance, particularly a good pitting corrosion resistance, and on the other hand to form, together with carbon, a desired amount of carbides.
  • molybdenum and tungsten are strong ferrite formers. Therefore the steel must not contain more than max. 4.0 % (Mo + W/2), preferably max. 3.0 % (Mo + W/2), suitably max. 2.8 % (Mo + W/2).
  • a suitable range is 2.1-2.6 % (Mo + W/2).
  • the nominal content of Mo + W/2 is 2.3 %.
  • Tungsten does not provide the same improvements of the corrosion resistance and of the hardenability as molybdenum does. Besides, because of the atomic weight conditions, twice as much tungsten is required in comparison with molybdenum, which is a drawback. The content of tungsten in the steel therefore is limited to max. 1.0 %W. Another drawback with tungsten is that the taking care of any produced scrap is made difficult, i.e. the utilisation of rest products (scrap) which are produced in connection with the manufacturing and working of the steel to a final product.
  • the steel should not contain any intentionally added amount of tungsten, but can be tolerated as an unavoidable impurity in an amount of max. 0.4 %, preferably max. 0.3 %, in the form a residual element emanating from the raw materials used for the manufacturing of the steel.
  • Vanadium shall exist in the steel in an amount of at least 0.1 %, normally in an amount of 0.5-3.0 %, in order, together with carbon and existing nitrogen, to form said MC- carbides, -nitrides and/or -carbonitrides in the martensitic matrix of the steel in the hardened and tempered condition of the steel.
  • the steel contains at least 0.6 % V, suitably at least 0.7 % V and max. 2.0, suitably max. 1.5 % V.
  • the vanadium content should rest in the range 0.8-1.2 % V.
  • a nominal content of vanadium is 1.0 % V.
  • Niobium is also an element which can form MC-carbides, -nitrides and/or - carbonitrides, but for this purpose twice as much niobium is required in comparison with vanadium, which is a drawback. Further, niobium causes the carbides, nitrides, and/or carbonitrides to get a more edgy shape and they will also be larger than pure vanadium carbides, -nitrides, and/or -carbonitrides which may initiate ruptures or chippings, which reduces the toughness of the material.
  • niobium may exist only as an unavoidable impurity in an amount of ⁇ 0.1 % Nb, preferably max. 0.05 % Nb, in the form of a residual element emanating from used raw materials in connection with the manufacturing of the steel.
  • the steel need not and should not, contain any further alloy elements in significant amounts.
  • Some elements are explicitly undesired because they have an influence on the features of the steel in an undesired way. This is true, e.g. as far as phosphorus is concerned, which should be kept at as low level as possible, preferably at max. 0.05 %, most conveniently at max. 0.03 %, in order not to influence on the toughness of the steel in an unfavourable way.
  • the steel normally does not contain more than max. 0.1 %, preferably max. 0.05 %, and most conveniently max. 0.025 % S.
  • the given contents of phosphorus, sulphur, tungsten, nickel, and copper are the maximally allowed contents of said elements in the form of impurities in the preferred compositions.
  • the manufacturing of the steel material comprises, as above mentioned, preferably spray forming of a steel melt to form an ingot, which is hot worked to desired dimensions.
  • the delivery condition of the steel is the soft annealed condition, in which the steel material according to the invention has a hardness of 200-280 HB (Brinell- hardness), preferably 210-250 HB.
  • the product is heat treated by austenitising at a temperature between 1000 and 1150°C, preferably at a temperature between 1080 and 1120°C.
  • a suitable holding time at the austenitising temperature is 10-30 minutes. From the said austenitising temperature the steel is cooled to about ambient temperature or possibly lower, e.g. by sub-zero cooling down to -196°C in order to eliminate retained austenite. In order to achieve a desired secondary hardening, the product is tempered at least once, preferably twice, at a temperature between 150 and 650°C, preferably at a temperature between 200 and 250°C (low temperature tempering) or between 400 and 600°C (high temperature tempering). The product is cooled after each such tempering treatment.
  • the holding time at the tempering temperature may be 1- 10 hours.
  • the steel material according to the invention has been developed in the first place to be used for specific products as mentioned above, it should be understood that the steel may be employed also within other fields, where the features of the steel material are advantageous, e.g. for wear parts and other construction elements than fixtures and holders of the mentioned kind.
  • Fig. 1 shows the microstructure of a first steel according to the invention in lOOx magnification
  • Fig. 2 shows the same steel in 500x magnification
  • Fig. 3 shows the microstructure of a reference steel in the same magnification as Fig. 2, and
  • Fig. 4 shows the microstructure of a second steel according to the invention in lOOx magnification.
  • Steels No's. 2-8 are commercially available reference materials.
  • Steel No. 4 is a steel according to information from literature. In Table 3, the analysed compositions of steels No's. 1-3 and 9 and the nominal compositions of steels No's. 4-8, respectively, are given. The denomination n.a. indicates that the contents of the elements in question lie on an impurity level, but that they have not been analysed.
  • Steels No's. 1 and 9 were, as mentioned, made by spray forming; steels No's. 2 and 3 in a conventional way, and the other steels powder metallurgically.
  • the ingot of steel No. 1 was forged to the shape of bars of size 200x80 mm and size 0 125 mm, while the ingot of steel No. 9 was forged to the shape of a bar of size 280x135 mm.
  • the other steels were forged to the shape of bars with sizes in the range 0 30- 0 125 mm.
  • the materials were examined with reference to: • Microstructure
  • a comparatively even structure which contained about 10 vol-% of comparatively evenly distributed carbides, nitrides and/or carbonitrides, mainly chromium carbides, -nitrides and/or -carbonitrides, M 7 C 3 (about 9 vol-%), and a smaller fraction of vanadium carbides, -nitrides, and/or -carbonitrides.
  • Fig. 2 which shows the steel at a larger scale, however, shows that the structure contains regions having a higher carbide content, partly in the form of aggregates.
  • Steel No. 9 had a more even microstructure with a desired carbide content and without aggregations, Fig. 4.
  • the reference material which is shown in Fig. 2, had a substantially more coarse carbide network which impairs the toughness/ductility.
  • the hardness was measured in the soft annealed condition (Brinell-hardness, HB), in the hardened and tempered condition.
  • the austenitising temperature varied between 1030 and 1120°C. All steels except steel No. 3 were high temperature tempered at 500 or 525°C. Steel No. 3 was tempered at 150°C because of the low tempering resistance of that steel which made higher temperature impossible.
  • Table 5 The values obtained from the performed experiments and from information in the literature are given in Table 5 below. In this table, also the relative values of the pressure strength which are proportional to the hardness, are given. In this relative comparison between the examined steels, the best value (excellent) has been given the value 5 and the lowest value (poor in the comparison between the steels) has been given the value 1. Reference is also made to the information below the table.
  • the corrosion resistance of steels No's. 1, 2, 4-6, 8 and 9 was measured via generation of polarisation graphs in 0.05 M H 2 SO 4 in the high temperature tempered, 525°, condition of the steels.
  • the results are given in Table 4, which indicates measured corrosion current, i cr , at the active peak of the polarisation graph. The smaller the current, the better the corrosion resistance.
  • Table 4 Measured polarisation current, i cr , via generation of polarisation graphs.
  • Heat response means such features as the capability of the steels to be hardened to the desired hardness from moderately high austenitising temperatures, the need of possible sub-zero cooling, as well as the level of the necessary temperature, which conveniently should be at least 250°C but not higher than 550°C, features which have been used as a basis for the relative evaluation of the heat treatment response given in Table 5.
  • Table 5 When estimating the production economy, not only the manufacturing of ingots, slabs, or blooms have been considered but the total costs included from start to finish. It should be beyond dispute that powder metallurgy manufacturing is most expensive, which therefore has been afforded the relative value 1. It has also been assessed that the total costs for the conventional manufacturing of the qualified steels in question are higher than the total costs for a manufacturing which includes spray forming of ingots. Conventional manufacturing therefore has been afforded value 2, while spray forming based manufacturing has the relative value 3.
  • steels No. 1 and No. 9 obtained the highest total value of 28 and 29, respectively, and no feature has been estimated as poor, which indicates that these steels have a good combination of features.
  • Their combination of features, however, is not identical, which indicates that there is a possibility to select materials within the scope of the invention, having features which are adapted to different applications.

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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)
  • Heat Treatment Of Articles (AREA)

Abstract

La présente invention concerne un matériau d'acier possédant une bonne résistance à la corrosion et la composition chimique suivante, en pourcentage en poids : de 0,7 à 1,6 (C+N) dont un max. de 0,8 N ; de 0,1 à 2,0 Si ; de 0,1 à1,5 Mn ; de 14 à 19 Cr ; de traces jusqu'à un max. de 2,0 Ni ; de traces jusqu'à un max. de 2,0 Co ; de 1,5 à 4,0 (Mo+W/2), néanmoins au moins 1,0 Mo et un max. de 1,0 W ; de 0,5 à 3,0 V ; < de 0,1 Nb ; de traces jusqu'à un max. de 0,2 S ; le reste étant constitué de fer et d'impuretés en quantités normales. L'acier de l'invention est apte à être utilisé dans des éléments de construction, des dispositifs de serrage des pièces de machines d'usinage et des outils de moulage.
PCT/SE2003/000224 2002-02-15 2003-02-12 Materiau d'acier contenant des carbures et utilisation du materiau WO2003069009A1 (fr)

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AU2003206341A AU2003206341A1 (en) 2002-02-15 2003-02-12 Steel material containing carbides and use of the material

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SE0200430A SE521150C2 (sv) 2002-02-15 2002-02-15 Stålmaterial innehållande karbider samt användning av detta material
SE0200430-7 2002-02-15

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Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1736563A1 (fr) 2005-06-23 2006-12-27 Sintec HTM AG Alliage d'acier
EP1917375A1 (fr) * 2005-08-24 2008-05-07 Uddeholm Tooling Aktiebolag Alliage d'acier, et outils ou composants fabriques a partir de cet alliage d'acier
CN104002112A (zh) * 2014-05-20 2014-08-27 滁州迪蒙德模具制造有限公司 一种模具的加工方法
WO2015124169A1 (fr) * 2014-02-18 2015-08-27 Schmiedewerke Gröditz Gmbh Acier au chrome pour pièces de machines fortement sollicitées à l'usure, en particulier pour matrices à pelleter
CN112639148A (zh) * 2018-09-04 2021-04-09 国立大学法人东北大学 铁基合金及铁基合金的制造方法

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Publication number Priority date Publication date Assignee Title
EP0630984A1 (fr) * 1993-05-13 1994-12-28 Hitachi Metals, Ltd. Pièce en acier rapide à haute ténacité et procédé pour sa fabrication
SE514226C2 (sv) * 1999-04-30 2001-01-22 Uddeholm Tooling Ab Kallarbetsverktyg av stål, dess användning och tillverkning
SE516934C2 (sv) * 1999-10-05 2002-03-26 Uddeholm Tooling Ab Stålmaterial, dess användning och tillverkning
SE518678C2 (sv) * 2001-03-06 2002-11-05 Uddeholm Tooling Ab Föremål av stål

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0630984A1 (fr) * 1993-05-13 1994-12-28 Hitachi Metals, Ltd. Pièce en acier rapide à haute ténacité et procédé pour sa fabrication
SE514226C2 (sv) * 1999-04-30 2001-01-22 Uddeholm Tooling Ab Kallarbetsverktyg av stål, dess användning och tillverkning
SE516934C2 (sv) * 1999-10-05 2002-03-26 Uddeholm Tooling Ab Stålmaterial, dess användning och tillverkning
SE518678C2 (sv) * 2001-03-06 2002-11-05 Uddeholm Tooling Ab Föremål av stål

Cited By (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1736563A1 (fr) 2005-06-23 2006-12-27 Sintec HTM AG Alliage d'acier
EP1917375A1 (fr) * 2005-08-24 2008-05-07 Uddeholm Tooling Aktiebolag Alliage d'acier, et outils ou composants fabriques a partir de cet alliage d'acier
US20110297277A1 (en) * 2005-08-24 2011-12-08 Uddeholms Ab Steel alloy and tools or components manufactured out of the steel alloy
EP1917375A4 (fr) * 2005-08-24 2013-03-06 Uddeholms Ab Alliage d'acier, et outils ou composants fabriques a partir de cet alliage d'acier
US8440136B2 (en) * 2005-08-24 2013-05-14 Uddeholms Ab Steel alloy and tools or components manufactured out of the steel alloy
WO2015124169A1 (fr) * 2014-02-18 2015-08-27 Schmiedewerke Gröditz Gmbh Acier au chrome pour pièces de machines fortement sollicitées à l'usure, en particulier pour matrices à pelleter
CN104002112A (zh) * 2014-05-20 2014-08-27 滁州迪蒙德模具制造有限公司 一种模具的加工方法
CN112639148A (zh) * 2018-09-04 2021-04-09 国立大学法人东北大学 铁基合金及铁基合金的制造方法
EP3848478A4 (fr) * 2018-09-04 2021-11-24 Tohoku University Alliage à base de fer et procédé de production d'un alliage à base de fer

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TW200417613A (en) 2004-09-16

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