• 专利附录
  • 专利说明
  • 权利要求
  • 类似技术
  • 同族专利
  • 引用文献
  • 法律状态
  • 优先权
    • 专利摘要:
    ABSTRACTThe invention relates hot Work tool steel. The steel comprises the following main components (in Wt. %): C 0.27 - 0.385 Si 0.10 - 0.35Mn 0.2 - 0.8Cr 4.0 - 6.0Mo 2.0 - 2.9V 0.4 - 0.6l0 N 0.0l - 0.l2 balance optional elements, iron and impurities.
    公开号:SE1551702A1
    申请号:SE1551702
    申请日:2015-12-22
    公开日:2017-06-23
    发明作者:Medvedeva Anna；Andersson Jerker；Robertsson Rikard；NILSSON Cherin；Ejnermark Sebastian
    申请人:Uddeholms Ab；
    IPC主号:
    专利说明:

    HOT WORK TOOL STEEL TECHNICAL FIELD The invention relates to a hot Work tool steel.
    BACKGROUND OF THE INVENTION Vanadium alloyed matrix tool steels have been on market for decades and attained aconsiderable interest because of the fact that they combine a high Wear resistance Withan excellent dimensional stability and because they have a good toughness. These steelshave a Wide range of applications such as for die casting and forging. The steels aregenerally produced by conventional metallurgy followed by Electro Slag Remelting(ESR).
    Although the vanadium alloyed matrix tool steels produced by ESR have betterproperties than conventionally produced tool steels With respect to heat checking, grosscracking, hot Wear and plastic deforrnation, there is a need for further improvements inorder to reduce the risk for hot Work tool failure, such as heat checking and grosscracking in high pressure die casting. In addition, it Would be benef1cial to further improve the hot strength and temper resistance of hot Work tool steel.
    DISCLOSURE OF THE INVENTION The object of the present invention is to provide a hot Work tool steel having an improved property profile leading to an increased life of the tool.
    Another object of the present invention is to improve the heat checking, While stillmaintaining a good hot Wear resistance and a good resistance to gross cracking. Stillanother object is provide a steel composition, Which in powder form is suitable forAdditive Manufacturing (AM), in particular for making or repairing injection moulding tools and dies.
    The foregoing objects, as well as additional advantages are achieved to a significantmeasure by providing a hot work tool steel having a composition as set out in the alloy claims.
    The invention is defined in the claims.
    DETAILED DESCRIPTION The importance of the separate elements and their interaction with each other as well asthe limitations of the chemical ingredients of the claimed alloy are briefly explained inthe following. All percentages for the chemical composition of the steel are given inweight % (wt. %) throughout the description. The amount of hard phases is given involume % (vol. %). Upper and lower limits of the individual elements can be freely combined within the limits set out in the claims.
    Carbon (0.27 - 0.38 %) is to be present in a minimum content of 0.27 %, preferably at least 0.28, 0.29, 0.30,0.31, 0.32, 0.33 or 0.34 %. The upper limit for carbon is 0.38 % and may be set to0.37, 0.36 or 0.35%. Preferred ranges are 0.30 - 0.38 % and 0.33 - 0. 37 %. In any case,the amount of carbon should be controlled such that the amount of primary carbides ofthe type M23C6, MvCg and MÖC in the steel is limited, preferably the steel is free from such primary carbides.
    Silicon (0.10 - 0.35 %) Silicon is used for deoxidation. Si is present in the steel in a dissolved form. Si is astrong ferrite former and increases the carbon activity and therefore the risk for theformation of undesired carbides, which negatively affect the impact strength. Silicon isalso prone to interfacial segregation, which may result in decreased toughness andtherrnal fatigue resistance. Si is therefore limited to 0.35%. The upper limit may be0.34, 0.32, 0.31, 0.30, 0.29, 0.28, 0.27, 0.26, 0.25, 0.24, 0.23 and 0.22%. The lowerlimit may be 0.12, 0.14, 0.16, 0.18 and 020%. Preferred ranges are 0.10 - 0.25 % and0.15 - 0.24%.
    Manganese (0.2 - 0.8 %) Manganese contributes to improving the hardenability of the steel and together Withsulphur manganese contributes to improVing the machinability by forrning manganesesulphides. Manganese shall therefore be present in a minimum content of 0.2 %,preferably at least 0.3, 0.35, 0.4, 0.45 or 0.5 %. At higher sulphur contents manganesepreVents red brittleness in the steel. The steel shall contain maximum 0.8 %, preferably maximum 0.7, 0.6, 0.55 or 0.5 %.
    Chromium (4.0 - 6.0 %) Chromium is to be present in a content of at least 4.0 % in order to provide a goodhardenability in larger cross sections during heat treatment. If the chromium content istoo high, this may lead to the formation of high-temperature ferrite, Which reduces thehot-Workability. The loWer limit may be 4.l, 4.2, 4.3, 4.4, 4.5, 4.6, 4.7, 4.8 or 4.9%. Theupper limit may be 6.0, 5.8, 5.6, 5.5, 5.4, 5.2 or 5.l %.
    Molybdenum (2.0 - 2.9 %) Mo is known to have a Very faVourable effect on the hardenability. Molybdenum isessential for attaining a good secondary hardening response. The minimum content is2.00 %, and may be set to 2.05, 2.l, 2.2, 2.25 or 2.3 %. Molybdenum is a strong carbideforming element and also a strong ferrite former. The maximum content ofmolybdenum is therefore 2.9 %. Preferably Mo is limited to 2.8, 2.7, 2.6, 2.5, 2.4 or2.35 %.
    Vanadium (0.4 - 0.6 %) Vanadium forms eVenly distributed primary precipitated carbides and carbonitrides ofthe type V(N,C) in the matrix of the steel. This hard phase may also be denoted MX,Wherein M is mainly V but Cr and Mo may be present and X is one or more of C, N andB. Vanadium shall therefore be present in an amount of 0.4 - 0.6%. The upper limit maybe set to 0.59, 0.58, 0.57, 0.56 or 0.55 %. The lower limit may be 0.42, 0.44, 0.46, 0.48,0.50 or 0.52%.
    Ratio V/C (1.35 - 1.65) The present inventors have found that the tensile strength at room temperature and atelevated temperature is influenced by the ration of the carbide forrning elementvanadium to the carbon content in the steel. The reason is belived to be related to thefact that these properties depends both on the dissolved content of carbon in the matrixand on the precipitated carbon. Also the thougness is influenced by the ratio. For thesereasons it is preferable that the ratio is 1.35 - 1.65, preferably 1.40 - 1.60 or morepreferably 1.45 - 1.55.
    Aluminium (0.00l - 0.06 %) Aluminium is used for deoxidation in combination with Si and Mn. The lower limit isset to 0.001, 0.003, 0.005 or 0.007% in order to ensure a good deoxidation. The upperlimit is restricted to 0.06% for avoiding precipitation of undesired phases such as AlN.
    The upper limit may be 0.05, 0.04, 0.03, 0.02 or 0.015%.
    Nitrogen (0.01 - 0.12 %) Nitro gen is restricted to 0.01 - 0.12 % in order to obtain the desired type and amount ofhard phases, in particular V(C,N). When the nitrogen content is properly balancedagainst the vanadium content, vanadium rich carbonitrides V(C,N) will form. These willbe partly dissolved during the austenitizing step and then precipitated during thetempering step as particles of nanometer size. The therrnal stability of vanadiumcarbonitrides is considered to be better than that of vanadium carbides, hence thetempering resistance of the tool steel may be improved and the resistance against graingrowth at high austenitizing temperatures is enhanced. The lower limit may be 0.011,0.012, 0.013, 0.014, 0.015, 0.016, 0.017, 0.018, 0.019 or 0.02%. The upper limit may be0.11, 0.10, 0.09, 0.08, 0.07, 0.06, 0.05, 0.04 or 0.03 %.
    Hydrogen (S 0.0004 %) Hydrogen is known to have a deleterious effect on the properties of the steel and tocause problems during processing. In order to avoid problems related to hydrogen themolten steel is subjected to vacuum degassing. The upper limit is 0.0004% (4 ppm) andmay be limited to 3, 2.5, 2, 1.5 or 1 ppm.
    Nickel (S15 %) Nickel may be present in an amount of S1 .5 %. It gives the steel a good hardenabilityand toughness. However, because of the expense, the nickel content of the steel shouldbe limited. The upper limit may therefore be set to 1.0, 0.8, 0.5 or 0.3%. However, Ni isnorrnally not deliberately added.
    Copper (S 2.0%) Cu is an optional element, Which may contribute to increasing the hardness and thecorrosion resistance of the steel. If used, the preferred range is 0.02 - 1%. However, it isnot possible to extract copper from the steel once it has been added. This drastically makes the scrap handling more difficult. For this reason, copper is norrnally not deliberately added.
    Cobalt (í 8 %) Co is an optional element. Co causes the solidus temperature to increase and thereforeprovides an opportunity to raises the hardening temperature, Which may be 15 - 30 °Chigher than Without Co. During austenitization it is therefore possible to dissolve largerfraetion of carbides and thereby enhance the hardenability. Co also increases the MStemperature. However, large amount of Co may result in a decreased toughness andWear resistance. The maximum amount is 8 % and, if added, an effective amount maybe 2 - 6 %, in particular 4 to 5 %. However, for practical reasons, such as scraphandling, deliberate additions of Co is not made. The maximum impurity content may then be set to 1 %, 0.5%, 0.3 %, 0.2% or 01%.
    Tungsten (S 1 %) In principle, mo lybdenum may be replaced by twice as much With tungsten because oftheir chemical similarities. However, tungsten is expensive and it also eomplicates the handling of scrap metal. The maximum amount is therefore limited to 1 %, preferably 0.5 %, more preferably 0.3 % and most preferably no deliberate additions are made.
    Niobium (E 0.5%) Niobium is similar to vanadium in that it forms carbonitrides of the type M(N,C) andmay in principle be used to replace part of the vanadium but that requires the doubleamount of niobium as compared to vanadium. However, Nb results in a more angularshape of the M(N,C). The maximum amount is therefore 05%, preferably 0.05 % and most preferably no deliberate additions are made.
    Ti, Zr and TaThese elements are carbide forrners and may be present in the alloy in the claimedranges for altering the composition of the hard phases. However, norrnally none of these elements are added.
    Boron (S 0.01%) B may be used in order to further increase the hardness of the steel. The amount islimited to 0.01%, preferably 5 0.005%. A preferred range for the addition of B is 0.001- 0.004 %.
    Ca, Mg and REM (Rare Earth Metals)These elements may be added to the steel in the claimed amounts for modifying thenon-metallic inclusion and/or in order to further improve the machinability, hot Workability and/or Weldability.
    Impurity elements P, S and O are the main impurities, Which have a negative effect on the mechanicalproperties of the steel. P may therefore be limited to 003%, preferably to 0.01%. S maybe limited to 0.0015, 0.0010, 00008, 00005 or even 0.0001%. O may be limited to0.0015, 00012, 0.0010, 00008, 00006 or 0.0005%.
    Steel productionThe tool steel having the claimed chemical composition can be produced byconventional metallurgy including melting in an Electric Arc Fumace (EAF) and further refining in a ladle and vacuum treatment. Optionally the steel may be subjected to Electro Slag Remelting (ESR) in order to further improve the cleanliness and the microstructural homo geneity.
    Norrnally the steel is subj ected to hardening and tempering before being used.Austenitizing may be performed at an austenitizing temperature (T A) in the range of1000-1070 °C, preferably 1030 - 1050 °C. A typical TA is 1040 °C with a holding timeof 30 minutes followed by rapid quenching. The tempering temperature is chosenaccording to the hardness requirement and is performed at least twice at 600 - 650 °C for 2 hours (2X2h) followed by cooling in air.
    EXAMPLE 1In this example, a steel having the following composition was produced by EAF- melting, ladle refining and vacuum degassing (VD) (in wt. %): C 0.35Si 0.18Mn 0.47Cr 5.05Mo 2.34V 0.54Al 0.009P 0.005S 0.0003H 0.00005N 0.0051O 0.0006V/C 1.54 balance iron and impurities.
    After vacuum degassing the steel was subjected to nitrogen alloying by cored wire injection. The final nitrogen content after said trimming was 0.0142 wt. %.
    The steel was cast into ingots and subjected hot working.
    The steel was austenitized at 1040 °C for 30 minutes and hardened by gas quenchingand tempering twice at 600 °C for 2 hours (2X2h) followed by cooling in air.
    The effect of the nitrogen alloying on the composition of the matrix and the amount ofprimary MX at three different austenitizing temperatures was calculated using Thermo-Calc. The results are shown in Table 1.
    Table 1.
    Matrix composition (austenite) 0.0051 %N C Si Mn Cr Mo V Vol. (%) MX1030 °C 0.335 0.18 0.47 5.05 2.32 0.46 0,191040 °C 0.338 0.18 0.47 5.05 2.32 0.47 0.161050 °C 0.340 0.18 0.47 5.05 2.32 0.48 0.130.0142 %N C Si Mn Cr Mo V Vol. (%) MX1030 ”C 0.325 0.18 0.47 5.05 2.32 0.38 0.371040 “C 0.328 0.18 0.47 5.05 2.32 0.40 0.341050 ”C 0.331 0.18 0.47 5.05 2.32 0.41 0.30 Table 1 reveals that the amount of the undissolved hard phase (MX) in the nitrogenalloyed steel is signif1cantly higher than the amount in the unalloyed steel at all threetemperatures. The MX-phase is responsible for pinning the grain boundaries andthereby obstructs the grains from growing. Accordingly, the inventive nitrogenalloyed is less prone to grain growth at hardening temperatures. This was alsoconfirmed by experiments, which showed that the steel with the low nitrogen contenthad a marked increase in grain size at 1060 °C whereas the nitrogen alloyed steel wasstable against grain growth to a temperature exceeding 1080 °C. Accordingly, a higherhardening temperature may be used for the nitro gen alloyed steel without deleterious grain growth. Thereby it is possible to influence the balance of properties in the die material in order to reduce the propensity for heat checking and/or gross cracking and thereby extend the die life.
    EXAMPLE 2 An alloy Was melted in an induction furnace and subjected to Nitrogen gas (5N) atomizing.
    C 0.34Si 0.16Mn 0.44Cr 5.01Mo 2.33V 0.53Al 0.008N 0.044O 0.0024V/C 1.59 balance iron and impurities.
    The powder Was sieved to < 500 um, filled in steel capsules having a diameter of 63mm and a height of 150 mm. HIPing Was performed at a temperature of 1150 °C, theholding time Was 2 hours and the pressure 110 MPa. The cooling rate Was < 1 °C/s. Thematerial thus obtained Was forged at 1130 °C to the dimension 20x30 mm. Softannealing Was performed at 900 °C With a cooling rate of 10 °C/h down to 750 °C andthereafter cooling freely in air. The amount of undissolved MX Was higher than in theprevious example and the nitrogen content Was higher. Due to this fact and to the finedistribution of the nitrogen rich vanadium carbonitride (MX) the steel Was found to be very robust against grain groWth.
    EXAMPLE 3A poWder having the same composition as in Example 2 Was subj ected to sieving in order to obtain a poWder having a narroW grain size distribution in the range of 10 - 60 uni. It Was found that the powder could successfully be used for laser cladding repairsof dies as Well as for rapid prototyping of e.g. dies With conforrnal cooling channels.Accordingly, it Would appear that the steel alloy poWder is suitable for Additive Manufacturing.
    INDUSTRIAL APPLICABILITY The tool steel of the present inVention is useful in large dies requiring a goodhardenability and a good resistance against heat checking and gross cracking. Atoniizedpowder of the alloy can be used to produce HIPed products having superior structuraluniforrnity. Powder of the alloy can be used for producing or repairing dies, in particular by additiVe manufacturing n1ethods.
    权利要求:
    Claims (10)
    [1] 1. A steel for hot Working consisting of in Weight % (Wt.%): C 0.27 - 0.38Si 0.10 - 0.35Mn 0.2 - 0.8 Cr 4.0 - 6.0Mo 2.0 - 2.9 V 0.4 - 0.6 N 0.01 - 0.12H S 0.0004optionally one or n1ore ofAl 0.001 - 0.06Ni S 1.5 Cu S 2 Co S 8 W S 1 Nb S 0.5 Ti S 0.05 Zr S 0.05 Ta S 0.05 B S 0.01 Ca 0.00005 - 0.009Mg S 0.01REM S 0.2 S S 0.0015 balance Fe apart fron1 inipurities.
    [2] 2. A steel according to clain1 1 fialfilling at least one of the following requirements:C 0.30 - 0.38Si 0.15 - 0.30Mn 0.4 - 0.6 Cr 4.5 - 5.5M0 2.1 - 2.8 V 0.5 - 0.6 N 0.011 - 0.08H S 0.0003Cu 0.02 - 1 Co S 1 W S 0.3 Nb S 0.05 Ti S 0.01 Zr S 0.01 Ta S 0.01 B S 0.005 Se S 0.03 Mg S 0.001 Ca 0.00001 - 0.009V/C 1.35 - 1.65 and Wherein the inipurity contents of P, S and O fulf1ls the following requirements P S 0.03 S S 0.0010O S 0.0015
    [3] 3. A steel according to clain1 1 or 2 fulfilling at least one of the following requirements : C 0.33 - 0.38Si 0.15 - 0.29N 0.012 - 0.07H S 0.0002Cu 0.02 - 0.5 Co S 0.3 WBMgCaV/C
    [4] 4. A steel according to any of the preceding claims fulf1lling at least one of the 13 S 0.1 0.001 - 0.0040.00005 - 0.0010.0001 - 0.0091.40 - 1.60 following requirements: CuCo NbMgCaV/C
    [5] 5. A steel according to any of the preceding claims, Wherein the content of primary precipitated MX is 0.2 - 3 Vol. %, preferably 0.3 -1.0 Vol. %.
    [6] 6. A steel according to any of claims 1 - 3 or 5 fialfilling the following requirements: 0.33 - 0.370.16 - 0.260.45 - 0.554.8 - 5.2 2.2 - 2.6 0.51 - 0.580.011 - 0.056S 0.0003 0.02 - 0.3 S 0.3 S 0.1 S 0.05 0.0001 - 0.0010.0001 - 0.0011.45 - 1.55 S 0.01 S 0.0005 S 0.0008 14 C 0.30 - 0.38Si 0.15 - 0.30Mn 0.4 - 0.6Cr 4.5 - 5.5M0 2.1 - 2.8V 0.5 - 0.6N 0.01 - 0.08H S 0.0003
    [7] 7. A steel according to any of claims 1 - 3, 5 or 6 fulfilling the following requirements: C 0.33 - 0.37Si 0.16 - 0.26Mn 0.45 - 0.55Cr 4.8 - 5.2Mo 2.2 - 2.6 V 0.51 - 0.58N 0.011 - 0.07
    [8] 8. A steel according to any ofthe preceding claim, wherein the matrix comprisestempered martensite and/ or bainite and the amount of retained austenite is limited to s 6 vol. %, s 5 vol. %, s 4 vol. %, or s 2 vol. %.
    [9] 9. A steel according to any ofthe preceding claim, wherein the steel is provided inthe form of a powder, preferably having a size distribution in the range of 5 -150 um, more preferably in the range of 10 - 100 um or 10 - 60 um, wherein the means size ofthe powder particles preferably is in the range of 25-50 um.
    [10] 10. Use of a steel powder according to claim 9 for additive manufacturing, in particular for making of repairing injection moulding tools.
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    引用文献:
    公开号 | 申请日 | 公开日 | 申请人 | 专利标题
    SU1548253A1|1988-07-26|1990-03-07|Институт проблем литья АН УССР|Die steel|
    JPH06172943A|1992-12-09|1994-06-21|Hitachi Metals Ltd|Die for hot working excellent in wear resistance|
    AT217360T|1998-02-27|2002-05-15|Boehler Edelstahl Gmbh & Co Kg|IRON BASED ALLOY FOR USE AT RISED TEMPERATURES|
    SE511700C2|1998-03-23|1999-11-08|Uddeholm Tooling Ab|Steel material for cold working tools produced in a non-powder metallurgical manner and this way|
    SE511758C2|1998-03-27|1999-11-22|Uddeholm Tooling Ab|Steel material for hot work tools|
    US6019938A|1998-04-23|2000-02-01|A. Finkl & Sons Co.|High ductility very clean non-micro banded die casting steel|
    US6478898B1|1999-09-22|2002-11-12|Sumitomo Metal Industries, Ltd.|Method of producing tool steels|
    JP2001214238A|2000-01-28|2001-08-07|Hitachi Metals Ltd|Powder hot tool steel excellent in heat crack resistance and wear resistance and hot die|
    US7520942B2|2004-09-22|2009-04-21|Ut-Battelle, Llc|Nano-scale nitride-particle-strengthened high-temperature wrought ferritic and martensitic steels|
    SE529041C2|2005-08-18|2007-04-17|Erasteel Kloster Ab|Use of a powder metallurgically made steel|
    FR2893954B1|2005-11-29|2008-02-29|Aubert & Duval Soc Par Actions|STEEL FOR HOT TOOLS AND PART PRODUCED IN THIS STEEL AND METHOD FOR MANUFACTURING THE SAME|
    JP5212772B2|2006-09-15|2013-06-19|日立金属株式会社|Hot work tool steel with excellent toughness and high temperature strength|
    AT506790B1|2008-11-20|2009-12-15|Boehler Edelstahl Gmbh & Co Kg|HOT STEEL ALLOY|
    CN102264921B|2008-12-25|2015-09-09|日立金属株式会社|The quenching method of steel|
    SE536596C2|2011-03-04|2014-03-18|Uddeholms Ab|Hot work steel and a process for producing a hot work steel|
    JP5680461B2|2011-03-24|2015-03-04|山陽特殊製鋼株式会社|Hot work tool steel|
    JP6032881B2|2011-10-18|2016-11-30|山陽特殊製鋼株式会社|Hot mold steel|
    EP2662462A1|2012-05-07|2013-11-13|Valls Besitz GmbH|Low temperature hardenable steels with excellent machinability|
    CN103834869A|2012-11-22|2014-06-04|应振强|Novel 5Cr3MnSiMo1VBN impact resistance tool steel|
    CA2937998A1|2014-01-27|2015-07-30|Rovalma, S.A.|Centrifugal atomization of iron-based alloys|
    JP6366326B2|2014-03-31|2018-08-01|山陽特殊製鋼株式会社|High toughness hot work tool steel and manufacturing method thereof|
    JP6647771B2|2014-05-23|2020-02-14|大同特殊鋼株式会社|Mold steel and mold|CN107419181A|2017-07-15|2017-12-01|滁州凯旋模具制造有限公司|A kind of auto parts and components crack resistence stretching die|
    JP2019136799A|2018-02-07|2019-08-22|住友重機械ハイマテックス株式会社|Method for manufacturing tool material and tool material|
    JP2019173049A|2018-03-27|2019-10-10|山陽特殊製鋼株式会社|Powder for metal mold|
    US20210040591A1|2018-05-14|2021-02-11|Hitachi Metals, Ltd.|Additive layer manufactured hot work tool, method for manufacturing the same, and metal powder for additive layer manufacturing hot work tool|
    CN109852880A|2019-01-10|2019-06-07|上海大学|A kind of high heat-intensity hot-work die steel and its manufacturing method|
    DE102019111236A1|2019-04-30|2020-11-05|Voestalpine Böhler Edelstahl Gmbh & Co Kg|Steel material and process for its manufacture|
    CN110938772B|2019-11-15|2020-08-21|南华大学|C-N-O supersaturated solid solution martensitic stainless steel powder and preparation and cladding methods thereof|
    JP2021181591A|2020-05-18|2021-11-25|大同特殊鋼株式会社|Metal powder|
    法律状态:
    优先权:
    申请号 | 申请日 | 专利标题
    SE1551702A|SE539646C2|2015-12-22|2015-12-22|Hot work tool steel|SE1551702A| SE539646C2|2015-12-22|2015-12-22|Hot work tool steel|
    CA3009044A| CA3009044A1|2015-12-22|2016-11-28|Hot work tool steel|
    US16/064,699| US11131012B2|2015-12-22|2016-11-28|Hot work tool steel|
    KR1020187020831A| KR20190034491A|2015-12-22|2016-11-28|Hot working tool steel|
    MX2018007563A| MX2018007563A|2015-12-22|2016-11-28|Hot work tool steel.|
    SI201631249T| SI3394309T1|2015-12-22|2016-11-28|Hot work tool steel|
    RU2018126761A| RU2728149C2|2015-12-22|2016-11-28|Tool steel for hot processing|
    JP2018531092A| JP2019504197A|2015-12-22|2016-11-28|Hot work tool steel|
    ES16879476T| ES2878268T3|2015-12-22|2016-11-28|Hot Work Tool Steel|
    PCT/SE2016/051174| WO2017111680A1|2015-12-22|2016-11-28|Hot work tool steel|
    EP16879476.6A| EP3394309B1|2015-12-22|2016-11-28|Hot work tool steel|
    BR112018012850A| BR112018012850A2|2015-12-22|2016-11-28|hot work steel tool|
    CN201680075284.8A| CN108474085B|2015-12-22|2016-11-28|Hot-working tool steel|
    TW105139668A| TWI703223B|2015-12-22|2016-12-01|Hot work tool steel|
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