EP3050986B1 - High-speed-tool steel and method for producing same - Google Patents

High-speed-tool steel and method for producing same Download PDF

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EP3050986B1
EP3050986B1 EP14847363.0A EP14847363A EP3050986B1 EP 3050986 B1 EP3050986 B1 EP 3050986B1 EP 14847363 A EP14847363 A EP 14847363A EP 3050986 B1 EP3050986 B1 EP 3050986B1
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steel
less
high speed
speed tool
cooling
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German (de)
English (en)
French (fr)
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EP3050986A1 (en
EP3050986A4 (en
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Shiho Fukumoto
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Proterial Ltd
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Hitachi Metals Ltd
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    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • 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
    • 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
    • C22C38/40—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the present invention relates to a high speed tool steel to be used for a tool, such as a die or a punch, as well as a method for producing the same.
  • a low-alloy high speed tool steel As a material for various tools, such as a die or a punch, to be used for warm-to-hot working, hitherto, a low-alloy high speed tool steel has been used, having a toughness that is improved by reducing the content of C (carbon), and of Mo, W, and V, which form a carbide together with C, relative to the ingredient composition of SKH51, which is a typical steel type of high speed tool steels.
  • Patent Document 1 a high speed tool steel has been proposed (Patent Document 1 below) whose toughness is enhanced by the following: a steel ingot composed of the ingredient composition of the high speed tool steel is subjected to a soaking treatment at a high temperature of from 1,200 to 1,300°C, and then cooled at a cooling rate of 3°C/min or more until the surface temperature of the steel ingot reaches 900°C or lower, so that aggregation of a carbide in the structure after quenching and tempering can be suppressed, and as a result, the average particle diameter of a carbide is limited to 0.5 ⁇ m or less, which makes the distribution density of the same 80 x 10 3 mm 2 or higher.
  • Patent Document 1 Japanese Patent Application Laid-Open ( JP-A) No. 2004-307963
  • Patent Document 1 is effective in improving the toughness of a low alloy high speed tool steel.
  • An object of the present invention is to provide a high speed tool steel whose toughness is further improved, and a method for producing the same.
  • the toughness of a high speed tool steel can be further improved.
  • a numerical range expressed by "x to y" herein includes the values of x and y in the range as the minimum and maximum values, respectively.
  • a “hardness” expressed in unit “HRC” means herein a Rockwell hardness on C scale according to JIS G 0202(2013).
  • a high speed tool steel according to the invention includes by mass-%: C (carbon) at from 0.40 to 0.90%; Si (silicon) at 1.00% or less; Mn (manganese) at 1.00% or less; Cr (chromium) at from 4.00 to 6.00%; one or both of W (tungsten) and Mo (molybdenum) in a content determined by the relational expression (Mo+0.5W) of from 1.50 to 6.00%; and one or both of V (vanadium) and Nb (niobium) in a content determined by the relational expression (V+Nb) of from 0.50 to 3.00%, wherein the content of N (nitrogen) is 0.0200% or less by mass-%, and the balance includes Fe (iron) and impurities; and wherein the maximum value of the equivalent circle diameter of a carbide in a sectional structure is 1.00 ⁇ m or less.
  • the concept of "carbide” according to the invention in a sectional structure of a high speed tool steel includes not only a carbide free from nitrogen but also a carbide containing nitrogen (namely, carbonitride).
  • the N content in a high speed tool steel according to the invention is 0.0200% or less as described above.
  • N is an impurity element inevitably contained in a steel ingot after casting.
  • a steel ingot after casting may contain N ordinarily at approx. 0.0300% or more.
  • N is an element having strong affinity for V and Nb, which are elements forming a carbide.
  • the carbonitride is a thermally stable compound.
  • the N content in a high speed tool steel according to the invention is 0.0200% or less so as to suppress the formation amount of of the carbonitride.
  • the form of the carbonitride crystallized in a steel ingot can be changed to a form of a carbide not containing nitrogen.
  • a carbide not containing nitrogen can be easily dissolved in a matrix by a soaking treatment, etc. Therefore, by reducing the N content to 0.0200% or less, a carbide distributed in a high speed tool steel can be micronized, so that the toughness of a high speed tool steel can be improved.
  • the maximum value of the equivalent circle diameter of a carbide in a sectional structure is 1.00 ⁇ m or less.
  • the average particle diameter of a carbide in the high speed tool steel described in Patent Document 1 is 0.5 ⁇ m or less.
  • a carbide having an equivalent circle diameter higher than 1.00 ⁇ m is mainly a carbide that does not dissolve into a matrix (insoluble carbide) in a quenching step at the quenching temperature (an austenitizing temperature about 900°C or higher).
  • the maximum value of the equivalent circle diameter of a carbide in a sectional structure is 1.00 ⁇ m or less, and it is needless to say that the average particle diameter of a carbide may be 0.5 ⁇ m or less, insofar as the above condition is satisfied.
  • the toughness can be further improved compared to a conventional high speed tool steel (for example, a high speed tool steel described in Patent Document 1).
  • the N content in a high speed tool steel according to the invention is preferably 0.0180% or less, and more preferably 0.0150% or less.
  • the lower limit of the N content in a high speed tool steel according to the invention there is no particular restriction on the lower limit of the N content in a high speed tool steel according to the invention, and the lower limit of the N content may be, for example, 0.0005%, or 0.0010%.
  • the maximum value of the equivalent circle diameter of a carbide in a sectional structure of a high speed tool steel according to the invention is 1.00 ⁇ m or less as described above, but the maximum value of the equivalent circle diameter is preferably 0.90 ⁇ m or less, and more preferably 0.80 ⁇ m or less.
  • the distribution density of a carbide in a high speed tool steel according to the invention can be 80 x 10 3 rom -2 or higher.
  • the distribution density of a carbide is high, the prior austenite particle diameter after quenching and tempering can be reduced, so that the toughness of a high speed tool steel can be further enhanced.
  • a high speed tool steel when the carbide is examined, a high speed tool steel has generally a shape of one of various tool products.
  • a region apparently vulnerable to cracking due to the carbide in the shape of a tool product is, for example, a working surface of the tool product, especially a corner part in contact with another component (external corner, and internal corner) in the working surface. Therefore, as a region of a high speed tool steel for examining the carbide, a sectional structure including the corner part may be selected.
  • a carbide having a strong influence on the toughness of a tool is mainly a carbide that does not dissolve into a matrix (insoluble carbide) in a quenching step at the quenching temperature (an austenitizing temperature about 900°C or higher).
  • a high speed tool steel according to the invention has preferably a hardness of 45 HRC or higher.
  • a superior tensile strength can be imparted to tools.
  • the in-use hardness hardness at room temperature
  • superior tensile strength at a high temperature can be imparted.
  • the hardness of a high speed tool steel according to the invention is more preferably from 45 HRC to 60 HRC.
  • the ingredient composition of a high speed tool steel according to the invention is common to the ingredient composition of the high speed tool steel in Patent Document 1 in terms of a basic composition except the N content.
  • C is an element which forms a hard double carbide by bonding with a carbide forming element, such as Cr, Mo, W, V, and Nb, and thereby imparting abrasion resistance to a high speed tool steel. Further, a part of C dissolves in a matrix, and thereby strengthening the matrix. Further, due to the above, a part of C imparts hardness to a martensite structure after quenching and tempering. However, an excessive amount of C encourages segregation of a carbide. Therefore, the C content is set between 0.40 and 0.90%.
  • Si is ordinarily used in a melting step as a deoxidizing agent, and is an element that a cast steel ingot inevitably contains.
  • the Si content is set at 1.00% or less.
  • Si has an action to micronize a rod-like M 2 C-type primary carbide to spheres. Therefore, the Si content is preferably 0.10% or more.
  • the Si content is preferably 0.20% or less.
  • the Si content is 0.20% or less
  • the action to micronize a primary carbide to spheres tends to weaken. Therefore, when Si is 0.20% or less, the effect of decreasing the N content to 0.0200% or less, and the effect of limiting the maximum value of the equivalent circle diameter of a carbide in a sectional structure is 1.00 ⁇ m or less, can be obtained more remarkably compared to a case where Si is higher than 0.20%.
  • Mn is, similarly to Si, used in a melting step as a deoxidizing agent, and is an element that a cast steel ingot inevitably contains.
  • the Mn content is set at 1.00% or less.
  • Mn has an action to improve hardenability. Therefore, the Mn content is preferably 0.10% or more.
  • Cr is an element that bonds with C to form a carbide and improves the abrasion resistance of a high speed tool steel. Further, Cr is an element that contributes also to improvement of the hardenability of a high speed tool steel. However, when the Cr content is too high, stripe segregation is encouraged, and the toughness of a high speed tool steel decreases. Therefore, the Cr content is set between 4.00 and 6.00%.
  • W and Mo are elements that bond with C to form a carbide, and dissolve into a matrix during quenching to increase hardness, so as to improve the abrasion resistance of a high speed tool steel.
  • the content of W and Mo is too high, stripe segregation is encouraged, and the toughness of a high speed tool steel decreases.
  • the content of W and Mo means a content determined by the relational expression (Mo+0.5W).
  • Mo represents the content (%) of Mo (molybdenum)
  • W represents the content (%) of W (tungsten).
  • the content of one or both of W and Mo is set between 1.50 and 6.00% in terms of a content determined by the relational expression (Mo+0.5W).
  • a high speed tool steel according to the invention may contain one (either) of W and Mo, or contain two (both) of W and Mo. Namely, either of "Mo" and “W” in the relational expression (Mo+0.5W) may be 0%.
  • the W content in a high speed tool steel is preferably 3.00% or less (1.50% or less in terms of 0.5W in the relational expression (Mo+0.5W)).
  • V and Nb at content determined by relational expression (V+Nb) from 0.50 to 3.00%
  • V and Nb bond with C to form a carbide to improve the abrasion resistance and seizure resistance of a high speed tool steel.
  • V and Nb dissolve into a matrix during quenching and precipitate carbides that are minute and resistant to aggregation during tempering, so as to improve the softening resistance of a high speed tool steel in a high temperature environment, and impart superior high temperature load-carrying capacity thereto.
  • V and Nb micronize crystal grains and increase the A 1 transformation temperature, so as to improve the toughness and the heat crack resistance of a high speed tool steel.
  • the content of V and Nb is too high, a large carbide is formed, and cracking in use as a tool is encouraged.
  • the content of V and Nb means a content determined by the relational expression (V+Nb).
  • the content of one or both of V and Nb is set between 0.50 and 3.00% in terms of a content determined by the relational expression (V+Nb).
  • V represents the content (%) of V (vanadium)
  • Nb represents the content (%) of Nb (niobium).
  • a high speed tool steel according to the invention may contain one (either) of V and Nb, or contain two (both) of V and Nb. Namely, either of "V" and “Nb” in the relational expression (V+Nb) may be 0%.
  • the content determined by the relational expression (V+Nb) is preferably 1.50% or less.
  • a high speed tool steel according to the invention should preferably contain Nb (namely, the Nb content is higher than 0%).
  • Ni at preferably 1.00% or less
  • Ni imparts superior hardenability to a high speed tool steel. In this way, a martensite rich quenched structure can be formed, and the toughness intrinsic to a matrix itself can be improved.
  • the Ni content is preferably 1.00% or less.
  • the Ni content is preferably 0.05% or more.
  • Co has an effect of forming a protective oxide film, which is extremely compact and has excellent adhesiveness, on a tool surface, when the temperature of the tool in use is elevated. In this way, a metal contact between the tool surface and a mating material is reduced, so that a temperature increase of the tool surface is mitigated thereby imparting superior abrasion resistance to the tool. Further, by formation of the protective oxide film, the heat insulating effect is strengthened and the heat crack resistance is also improved.
  • the Co content is too high, the toughness of a high speed tool steel decreases. Consequently, even when a high speed tool steel contains Co, the Co content is preferably 5.00% or less. And, when a high speed tool steel contains Co, the Co content is preferably 0.30% or more.
  • a high speed tool steel according to the invention possibly contains, for example, S (sulfur), or P (phosphorus) as an unavoidable impurity element.
  • the S content is preferably adjusted to 0.0100% or less.
  • the S content is more preferably 0.0050% or less.
  • the P content is preferably adjusted to 0.050% or less.
  • the P content is more preferably 0.025% or less.
  • a method for producing a high speed tool steel according to the invention there is no particular restriction on a method for producing a high speed tool steel according to the invention.
  • a soaking treatment preferably, a soaking treatment in which the steel ingot is heated to between 1200 and 1300°C
  • cooling preferably, cooling in which the steel ingot after the soaking treatment is cooled until the surface temperature of the steel ingot reaches 900°C or less
  • hot working preferably, hot working in which the cooled steel ingot is reheated higher than 900°C
  • quenching and tempering preferably, quenching and tempering in which the quenching temperature is 900°C or more, and the tempering temperature is from 500 to 650°C
  • a steel material may be machined to a tool shape between the hot working and the quenching and tempering.
  • a high speed tool steel according to the invention can be especially easily produced.
  • a method for producing a high speed tool steel according to the invention includes:
  • a cooling rate of the surface temperature of a steel ingot may be herein simply referred to as a "cooling rate”.
  • the present inventors investigated deeply the method for producing a high speed tool steel including a soaking treatment proposed in Patent Document 1. As the result, it has been confirmed that a high temperature soaking treatment between 1,200 and 1,300°C is effective indeed for dissolving a carbide in a steel ingot of a high speed tool steel having a low alloy ingredient composition as in Patent Document 1.
  • the inventors have also observed that in a case in which the control of a cooling process after the soaking treatment is inappropriate, a carbide which is insoluble or newly precipitated may occasionally grow coarser. Now, the inventors have finally found out that by an appropriate control of the cooling conditions the growth of a carbide in a cooling process can be suppressed, and as the result a carbide in the structure of a high speed tool steel can be micronized. Further, the inventors have found out that for keeping the effect of micronization of a carbide by appropriate cooling conditions, there is an especially suitable ingredient composition of an steel ingot itself which is an object of the soaking treatment, thereby completing a method for producing a high speed tool steel according to the invention.
  • a steel ingot with a N content of 0.0200% or less by mass-% is used.
  • a carbide distributed in a produced high speed tool steel can be micronized as described in a section concerning "high speed tool steel", and therefore a high speed tool steel with improved toughness can be produced.
  • regulation of the N content in a steel ingot which is an object of the soaking treatment at 0.0200% or less plays an important role together with a cooling step in the present producing method in micronizing a carbide (including carbonitride) in a structure.
  • a carbide including carbonitride
  • the carbide crystallized in a steel ingot can be dissolved into a matrix in the next soaking treatment step at from 1,200 to 1,300°C. Then in a cooling process after the soaking treatment, precipitation and growth of a carbide of V or Nb can be suppressed by cooling the surface temperature of a steel ingot to 900°C or less at a cooling rate of 3°C/min or more.
  • the temperature at which the carbide precipitates and grows in the cooling process after the soaking treatment can be lowered.
  • the temperature at which the carbide precipitates and grows can be lowered to 1,000°C or less in terms of the surface temperature of a steel ingot.
  • the present producing method by using a steel ingot with a N content of 0.0200% or less as an object of the soaking treatment, and by providing a cooling step in which the steel ingot is cooled such that at least after the surface temperature of a steel ingot has decreased to a temperature T1 within a range of not higher than 1,000°C but higher than 900°C, the cooling rate of the surface temperature is 3°C/min or more until the surface temperature reaches 900°C or less, micronization of a carbide can be achieved more surely. Therefore, by the present producing method, a high speed tool steel having improved toughness compared to a conventional high speed tool steel (for example, a high speed tool steel described in Patent Document 1) can be produced.
  • a high speed tool steel in which the maximum value of the equivalent circle diameter of a carbide in a sectional structure is 1.00 ⁇ m or less (for example, the high speed tool steel according to the invention) can be produced.
  • a preparation step is a step for preparing a steel ingot including by mass-%: C at from 0.40 to 0.90%; Si at 1.00% or less; Mn at 1.00% or less; Cr at from 4.00 to 6.00%; one or both of W and Mo in a content determined by the relational expression (Mo+0.5W) of from 1.50 to 6.00%; and one or both of V and Nb in a content determined by the relational expression (V+Nb) of from 0.50 to 3.00%, wherein the content of N is 0.0200% or less by mass-%, and the balance includes Fe and impurities.
  • the preparation step is a step for the sake of convenience.
  • the preparation step may be a step for producing a steel ingot, or may be a step for preparing a steel ingot produced in advance prior to the production of a high speed tool steel.
  • the ingredient composition of a steel ingot to be prepared in a preparation step is the same as the ingredient composition of a high speed tool steel according to the invention, and the preferable range is also the same.
  • a steel ingot to be prepared in a preparation step in the present producing method is preferably a steel ingot yielded by casting a molten steel refined by a deoxidizing refining method.
  • Examples of a deoxidizing refining method include various ladle refining methods, such as a LF method, an ASEA-SKF method, a VAD method, and a VOD method; and various vacuum degassing methods, such as a RH method, and a DH method.
  • each single steel ingot is massive, and segregation in a steel ingot may become severe.
  • a steel ingot to be prepared in a preparation step is more preferably a steel ingot, which is yielded by casting a molten steel refined by a deoxidizing refining method to an electrode for remelting, and by subjecting the yielded electrode for remelting to a remelting method.
  • a remelting method segregation in a steel ingot can be mitigated.
  • Examples of a remelting method include an electro-slag remelting method, a vacuum arc remelting method, a plasma arc remelting method, and an electron beam remelting method.
  • an electro-slag remelting method is advantageous for reducing an impurity element such as S, because slag is used.
  • a soaking treatment step is a step for conducting a soaking treatment by heating a steel ingot prepared in the preparation step at from 1,200 to 1,300°C.
  • a soaking treatment step by subjecting a steel ingot with the ingredient composition to a soaking treatment at a high temperature of from 1,200 to 1,300°C similarly as the technique according to Patent Document 1, so that a very large carbide present in casting is dissolved, and composition ingredients are dissolved and dispersed, and that the distribution of a carbide can be improved.
  • the temperature for a soaking treatment is from 1,200 to 1,300°C, it is preferably from 1,260 to 1,300°C.
  • the duration of a soaking treatment is preferably from 10 to 20 hours.
  • an ordinary temperature of a soaking treatment for a high speed tool steel is around 1,150°C, and the temperature of a soaking treatment according to the present producing method is higher than the ordinary temperature of a soaking treatment.
  • a cooling step is a step for cooling a steel ingot after the soaking treatment step until the surface temperature of the steel ingot reaches 900°C or less, such that in the course of cooling down of the surface temperature of the steel ingot to 900°C or less at least after the surface temperature of the steel ingot has decreased to a temperature T1 within a range of not higher than 1,000°C but higher than 900°C, cooling is performed at a cooling rate of the surface temperature of the steel ingot of 3°C/min or more.
  • a cooling step cooling at a cooling rate of 3°C/min or more is carried out until the surface temperature of the steel ingot reaches 900°C or less.
  • the cooling step is a step by which a temperature range down to 900°C, where carbides of V and Nb are apt to precipitate and grow, is passed through quickly so as to suppress formation of a coarse particle of a carbide, and preferably to form solely small particles of a carbide finely dispersed in a matrix.
  • the N content in a steel ingot which is an object of a soaking treatment is limited to 0.0200% or less, and as the result the temperature of precipitation and growth of a carbide in the course of cooling can be successfully lowered to approx. 1,000°C.
  • a cooling step cools a steel ingot after the soaking treatment step until the surface temperature of the steel ingot reaches 900°C or less, such that in the course of cooling down of the surface temperature to 900°C or less at least after the surface temperature has decreased to a temperature T1 within a range of not higher than 1000°C but higher than 900°C, cooling is performed at a cooling rate of the surface temperature of 3°C/min or more.
  • cooling until the surface temperature of a steel ingot declines to the temperature T1 may be performed at a cooling rate of the surface temperature of below 3°C/min, however it may also be performed at a cooling rate of the surface temperature of 3°C/min or more.
  • the cooling rate of 3°C/min or more can be achieved, for example, by air cooling (radiational cooling) or fan cooling on a steel ingot taken out from a soaking treatment furnace.
  • the temperature T1 is a temperature that falls within a range of not higher than 1,000°C but higher than 900°C, preferably a temperature that falls within a range of from 1,000°C to 950°C, more preferably a temperature that falls within a range of from 1,000°C to 970°C, and especially preferably 1,000°C.
  • a cooling step is preferably a step in which cooling is performed, at least after the surface temperature of a steel ingot is cooled down to 950°C, at a cooling rate of the surface temperature of a steel ingot of 3°C/min or more until the surface temperature of the steel ingot reaches 900°C or less.
  • a cooling step is more preferably a step in which cooling is performed, at least after the surface temperature of a steel ingot is cooled down to 1,000°C, at a cooling rate of the surface temperature of a steel ingot of 3°C/min or more until the surface temperature of the steel ingot reaches 900°C or less.
  • a cooling rate after cooled down to the temperature T1 is 3°C/min or more, and the cooling rate is preferably 10°C/min or more, more preferably 20°C/min or more, further preferably 30°C/min or more, and especially preferably 40°C/min or more.
  • the upper limit of a cooling rate after cooled down to the temperature T1 there is no particular restriction on the upper limit of a cooling rate after cooled down to the temperature T1, and the upper limit is preferably 100°C/min, and more preferably 80°C/min.
  • a hot working step is a step for reheating a steel ingot after the cooling step to a hot working temperature higher than 900°C, and hot-working the reheated steel ingot into a steel product.
  • the hot working temperature means a temperature for initiating the hot working.
  • Hot working is performed for purposes of improvement of a cast structure of a steel ingot, adjustment to a predetermined size of a steel material, etc.
  • Hot working may be carried out following prevailing cogging conditions of forging, rolling, etc.
  • a hot working temperature of a steel ingot after the cooling step is higher than 900°C, preferably 950°C or more, more preferably 1,000°C or more, and especially preferably 1,050°C or more.
  • the upper limit of a hot working temperature of a steel ingot after the cooling step is preferably 1,250°C, more preferably 1,200°C, and especially preferably 1,150°C.
  • a quenching and tempering step is a step for quenching and tempering a steel material yielded by the hot working.
  • a steel material after quenching and tempering is superior in toughness, since a carbide contained in a structure is adjusted to minute particles.
  • Quenching and tempering in a quenching and tempering step may be carried out by the same methods as in Patent Document 1, and carried out according to prevailing conditions, etc.
  • a quenching temperature may be selected appropriately in a range of 900°C or higher.
  • a quenching temperature is more preferably 950°C or more, and further preferably 1,000°C or more.
  • a tempering temperature may be appropriately selected in a range of from 500 to 650°C.
  • a quenching and tempering step is preferably a step for adjusting the hardness of a steel material (steel product) by quenching and tempering to 45 HRC or more (more preferably from 45 to 60 HRC).
  • the hardness of a steel product after quenching and tempering in the step is preferably 45 HRC or more (more preferably from 45 to 60 HRC).
  • the present producing method may further include a machining step for machining the steel material into a tool shape after the hot working step and before the quenching and tempering step, and the quenching and tempering step may be a step for quenching and tempering the steel material machined into a tool shape.
  • Such a mode of the present producing method can produce a steel material in a tool shape (namely, tool product) efficiently.
  • the state of a steel material after hot working is preferably an annealed state with a low hardness.
  • it is efficient to machine a steel material in such an annealed state, and thereafter to conduct quenching and tempering.
  • a molten steel adjusted to a predetermined ingredient composition was prepared by an atmospheric dissolving method.
  • the molten steel was subjected further to refining by a ladle refining method to lower the N content.
  • the molten steel (with respect to a molten steel to be used for Inventive Example is a molten steel adjusted to a low N content) was cast to prepare an electrode (electrode for remelting) for electro-slag remelting.
  • electro-slag remelting was conducted on the electrode to produce a steel ingot A or a steel ingot B of a high speed tool steel having an ingredient composition listed in Table 1 in which the balance was Fe and impurities.
  • a soaking treatment was conducted on each of the steel ingot A and the steel ingot B, by which the ingot was kept at 1,280°C for 10 hours (soaking treatment step), then cooled under any one of the cooling conditions 1 to 4 presented in Figure 1 (cooling step).
  • the cooling condition 1 is a cooling condition, under which a steel ingot after a soaking treatment is cooled slowly (cooling rate: 0.5°C/min) until the surface temperature of the steel ingot decreases from a soaking treatment temperature (1,280°C) to 1,200°C, and after the surface temperature of the steel ingot is lowered to 1,200°C air cooling by fan cooling (cooling rate: approx. 50°C/min) is conducted until the surface temperature of the steel ingot reaches 900°C or less.
  • the cooling condition 2 is a condition, under which the temperature for switching from slow cooling to air cooling in the cooling condition 1 is changed from 1,200°C of the cooling condition 1 to 1,100°C.
  • the cooling condition 3 is a condition, under which the temperature for switching from slow cooling to air cooling in the cooling condition 1 is changed from 1,200°C of the cooling condition 1 to 1,000°C.
  • the cooling condition 4 is a condition, under which the temperature for switching from slow cooling to air cooling in the cooling condition 1 is changed from 1,200°C of the cooling condition 1 to 900°C.
  • Figure 2 shows a binarized image for each steel ingot.
  • carbides appear as dispersed black spots.
  • the steel ingot A (N at 0.0128%) cooled under the cooling condition 1 (after a soaking treatment, cooled slowly to 1,200°C) in Example 1, and the steel ingot B (N at 0.0296%) cooled under the cooling condition 1 (after a soaking treatment, cooled slowly to 1,200°C) in Example 1 were respectively reheated to a hot working temperature of 1,100°C, and the reheated steel ingots were hot-pressed and hot-rolled for cogging.
  • the respective cogged steel ingots (billets) were subjected to hot rolling to complete round bar steel materials with a cross-section diameter of 100 mm (hot working step).
  • a portion was sampled from each round bar steel material and each of the obtained sample was subjected to quenching from 1,080°C and tempering at 560°C to obtain an evaluation sample (high speed tool steel) adjusted to a hardness of 56 HRC (quenching and tempering step).
  • evaluation samples for Inventive Example high speed tool steel produced using the steel ingot A
  • evaluation samples for Comparative Example high speed tool steel produced using the steel ingot B
  • Figure 3 is a scanning electron micrograph of a sectional structure of an evaluation sample of Inventive Example (high speed tool steel produced using the steel ingot A), and Figure 4 is a scanning electron micrograph of a sectional structure of an evaluation sample of Comparative Example (high speed tool steel produced using the steel ingot B).
  • the particle size distribution of a carbide was measured by examining a relationship between an equivalent circle diameter of a carbide and a number density (mm -2 ).
  • Figure 5 is a graph showing the relationship between an equivalent circle diameter and a number density (mm -2 ) of a carbide.
  • total 176 x 10 3 mm -2 or “total 180 x 10 3 mm -2” in Figure 5 refers to a number density of all carbides (mm -2 ) obtained by summing up each number density of an equivalent circle diameter.
  • a carbide in a high speed tool steel of Inventive Example is finer than a carbide in a high speed tool steel of Comparative Example. Further, in a high speed tool steel of Inventive Example, a number density of all carbides was 80 x 10 3 mm -2 or more indicating that a large number of fine carbides were formed.
  • the notch shape of a specimen for a Charpy impact test was 10R.
  • a high speed tool steel material of Inventive Example had a larger Charpy impact value than a high speed tool steel of Comparative Example, and was superior in toughness.
  • Figure 6 and Figure 7 are individually a scanning electron micrograph showing a fracture surface near a notch after a Charpy impact test on a specimen TP2 cut out in a radial direction of a round bar steel material with respect to a high speed tool steel of Inventive Example or Comparative Example.

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  • Organic Chemistry (AREA)
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  • Physics & Mathematics (AREA)
  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Articles (AREA)
  • Manufacture And Refinement Of Metals (AREA)
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CN107177800A (zh) * 2017-05-14 2017-09-19 合肥鼎鑫模具有限公司 一种数控铣床铣刀用高速工具钢及其制造方法
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CN109988971B (zh) * 2019-04-16 2020-05-08 东北大学 一种生产特超级纯净高速工具钢的方法
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CN113604730A (zh) * 2021-07-05 2021-11-05 昆山东大特钢制品有限公司 一种耐高温和高韧性的热作模具钢及其生产工艺
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Publication number Priority date Publication date Assignee Title
DE102021101105A1 (de) 2021-01-20 2022-07-21 Voestalpine Böhler Edelstahl Gmbh & Co Kg Verfahren zur Herstellung eines Werkzeugstahls als Träger für PVD-Beschichtungen und ein Werkzeugstahl
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JP6474348B2 (ja) 2019-02-27
CN105579604A (zh) 2016-05-11
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WO2015045528A1 (ja) 2015-04-02
TW201527549A (zh) 2015-07-16

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