EP2733229B1 - Walzdraht mit hervorragender wasserstoffverzögerter bruchfestigkeit, herstellungsverfahren dafür, hochfester schraubbolzen damit und verfahren zur herstellung des bolzens - Google Patents

Walzdraht mit hervorragender wasserstoffverzögerter bruchfestigkeit, herstellungsverfahren dafür, hochfester schraubbolzen damit und verfahren zur herstellung des bolzens Download PDF

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Publication number
EP2733229B1
EP2733229B1 EP12814354.2A EP12814354A EP2733229B1 EP 2733229 B1 EP2733229 B1 EP 2733229B1 EP 12814354 A EP12814354 A EP 12814354A EP 2733229 B1 EP2733229 B1 EP 2733229B1
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EP
European Patent Office
Prior art keywords
wire rod
bolt
precipitate
delayed fracture
fracture resistance
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EP12814354.2A
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English (en)
French (fr)
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EP2733229A1 (de
EP2733229A4 (de
EP2733229B9 (de
Inventor
You-Hwan Lee
Dong-Hyun Kim
Geun-Soo RYU
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Posco Holdings Inc
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Posco Co 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/0093—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for screws; for bolts
    • 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
    • C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/525—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length for wire, for rods
    • 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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium

Definitions

  • the present disclosure relates to a wire rod used for automobile engine bolts and the like, and more particularly, to a wire rod having improved hydrogen delayed fracture resistance, a method for manufacturing the same, a high strength bolt using the same, and a method for manufacturing the bolt.
  • the drawn wire after performing wire drawing intended for sizing, through low temperature annealing, the drawn wire may be subjected to spheroidizing heat treatment, bolt-forming, quenching and tempering processes to finally obtain a steel having a single-phase structure composed of tempered martensite.
  • strength of the bolt may be determined depending on composing, quenching, tempering and heat treatment processes performed thereon.
  • the wire rod as a raw material needs to have as little strength as possible in order to facilitate bolt-forming.
  • alloying elements in particular, carbon elements
  • DBTT brittle transition temperature
  • work hardening may be increased, causing disadvantages in bolt-forming and a separate softening heat treatment may be required.
  • Bolts manufactured as described above may generally have a tempered martensite structure in which carbide precipitates are distributed in grain boundaries or grains and the basic material thereof has precipitates distributed in lath martensite.
  • a main factor hindering the high strengthening of the basic material may be a degradation in delayed fracture resistance due to the introduction of hydrogen, and it has been known because the introduced hydrogen may deteriorate the strength of grain boundaries.
  • an operation for improving delayed fracture resistance may be required.
  • improvements in delayed fracture resistance may be unavoidably required to increase critical delayed fracture strength, and to this end, a method of generating precipitates capable of trapping diffusible hydrogen or controlling a microstructure by adding certain elements while maximally suppressing phosphorus (P) and sulfur (S) brominating austenitic grain boundaries, and the like may be present.
  • the related art technologies for improving hydrogen delayed fracture resistance may include 1) corrosion suppression in steel, 2) minimization of an amount of introduced hydrogen, 3) suppression of diffusible hydrogen contributing to delayed fracture, 4) the use of steel having a high concentration of limited diffusible hydrogen contained therein, 5) minimization of tensile stress, 6) stress concentration reduction, 7) miniaturization of austenite grain boundary size, and the like.
  • a method of achieving improvements in hydrogen delayed fracture resistance a method of implementing a high degree of alloying, or a surface coating method or a plating method for preventing the introduction of external hydrogen has been mainly used.
  • a technology of improving delayed fracture characteristics of a high strength wire rod having a tensile strength of 1600 MPa or greater, using complete pearlite is present.
  • 0.2 wt% or more of chromium needs to be added in order to improve tensile strength through wire drawing and to secure drawability during wire drawing intended for sizing after the production of a wire rod, and lead patenting for isothermal transformation may necessarily be required.
  • such a technology may have disadvantages such as high manufacturing costs and complex processes and have limitations such as the requirement for excessively precise rolling and cooling conditions at the time of manufacturing steel.
  • the tensile strength may be secured without a final heat treatment, unlike in other technologies.
  • the technology basically aims at improving hydrogen delayed fracture resistance by adding a great quantity of molybdenum (Mo), it may be disadvantageous in terms of high manufacturing costs.
  • Document JP55884960 A relates to a high strength bolt having a tensile strength ⁇ 120 kg/mm 2 and superior delayed rupture resistance.
  • An aspect of the present disclosure provides a wire rod having superior hydrogen delayed fracture resistance while securing ultrahigh strength through a heat treatment, and a method for manufacturing the same.
  • An aspect of the present disclosure also provides a high strength bolt having superior hydrogen delayed fracture resistance using the wire rod, and a method for manufacturing the same.
  • a wire rod according to claim 1 having superior hydrogen delayed fracture resistance and having a composition consisting of C: 0.3 to 0.7 wt%, Si: 0.05 to 2.0 wt%, Mn: 0.7 to 1.5 wt%, La: 30 to 70ppm, Ni : 0.01 to 0.1%, the balance being Fe and inevitable impurities.
  • a method for manufacturing a wire rod having superior hydrogen delayed fracture resistance including: heating a steel having a composition consisting of C: 0.3 to 0.7 wt%, Si: 0.05 to 2.0 wt%, Mn: 0.7 to 1.5 wt%, La: 30 to 70ppm, Ni: 0.01 to 0.1%, the balance being Fe and inevitable impurities to a temperature of Ae3+150°C to Ae3+250°C; cooling the heated steel at a rate of 5 to 15°C/s and rolling the steel at a temperature of Ae3+50°C to Ae3+150°C to manufacture a wire rod; and cooling the rolled wire rod to 600 °C or less at a rate of 0.5 to 3°C/s.
  • a bolt having a composition consisting of C: 0.3 to 0.7 wt%, Si: 0.05 to 2.0 wt%, Mn: 0.7 to 1.5 wt%, La: 30 to 70ppm, Ni: 0.01 to 0.1%, the balance being Fe and inevitable impurities, and having a tensile strength of 1200 MPa or greater and superior hydrogen delayed fracture resistance, as defined in claim 6.
  • a method for manufacturing a bolt having superior hydrogen delayed fracture resistance including: heating a steel having a composition consisting of C: 0.3 to 0.7 wt%, Si: 0.05 to 2.0 wt%, Mn: 0.7 to 1.5 wt%, La: 30 to 70ppm, Ni : 0.01 to 0.1%, the balance being Fe and inevitable impurities to a temperature of Ae3+150°C to Ae3+250°C; cooling the heated steel at a rate of 5 to 15°C/s and rolling the steel at a temperature of Ae3+50°C to Ae3+150°C to manufacture a wire rod; cooling the rolled wire rod to 600°C or less at a rate of 0.5 to 3°C/s; and bolt-forming using the cooled wire rod; performing a heat treatment on the formed bolt at a temperature of 850 to 950°C; and performing quenching after the heat treatment, and then performing tempering at a temperature of 300
  • the wire rod according to the present disclosure may be a high strength wire rod used for the coupling of automobile components or used in such automobile components, and the method of manufacturing the wire rod may be advantageous in that a wire rod having high strength of 1200 MPa to 2000 MPa and superior hydrogen delayed fracture resistance, even in a case in which a tiny amount of lanthanum and nickel is added or even in a case in which a martensite microstructure is present after the final heat treatment, may be manufactured with low manufacturing costs.
  • the stability of a steel structure may be increased due to a reinforcement of coupling force and a reduction of vacancies in a coupling part at the time of coupling the bolts, and an amount of steel used may be reduced due to a decrease in the number of coupled bolts.
  • the development of the wire rod for bolts as described above may contribute to lightening of the automobile components. Due to the lightening of automobile components, various automobile assembling device designs may be enabled and compactness of automobile assembling devices may be allowed.
  • a wire rod according to an exemplary embodiment of the present disclosure will be described in detail.
  • a compositional range of the wire rod according to the exemplary embodiment of the present disclosure will be described (hereinafter, referred to as weight percentage (wt%)).
  • Carbon (C) is included in the wire rod in an amount of 0.3 to 0.7 wt%.
  • carbon (C) is included in an amount exceeding 0.7 wt%, although the wire rod may be frequently used in the form of a high carbon wire rod formed using common cold wire drawing, in a case in which the wire rod is subjected to a heat treatment suggested in the exemplary embodiment of the present disclosure, film shaped carbides may be frequently eluted in austenite grain boundaries to thereby deteriorate hydrogen delayed fracture resistance.
  • an amount of carbon (C) exceeding 0.7 wt% is not preferable.
  • carbon (C) when carbon (C) is included in an amount less than 0.3 wt%, since tensile strength of a bolt may be insufficiently secured through quenching and tempering heat treatments, carbon (C) is added in an amount of 0.3 wt% or greater in order to secure a sufficient degree of strength.
  • Silicon (Si) is included in the wire rod in an amount of 0.05 to 2.0 wt%.
  • silicon (Si) is included in an amount exceeding 2.0 wt%, a work hardening phenomenon may be rapidly generated during a cold forging process for manufacturing bolts to deteriorate processability.
  • silicon (Si) is included in an amount less than 0.05 wt%, a sufficient degree of strength may not be secured and spheroidization of cementite may also be adversely affected.
  • Manganese (Mn) is included in the wire rod in an amount of 0.7 to 1.5 wt%.
  • Manganese (Mn) an element forming a substitutional solid solution in a base structure to perform solid solution reinforcement, may be very useful in high tension bolt characteristics.
  • Mn manganese
  • a heterogeneous structure caused by manganese segregation may have a negative influence on bolt characteristics, rather than having solid solution reinforcement effects.
  • the segregation area may be barely affected by the manganese segregation, but tensile strength of a final product may not be secured through solid solution reinforcement. That is, when manganese (Mn) is included in an amount less than 0.7 wt%, improvements in quenching and permanent deformation resistance may be insufficient due to insufficient solid solution reinforcement.
  • Nickel (Ni) is included in the wire rod in an amount of 0.01 to 0.1 wt%.
  • Nickel (Ni) may be a very important element forming a compound within a grain boundary, together with lanthanum (La).
  • La lanthanum
  • nickel (Ni) is included in an amount less than 0.01 wt%, an effective compound, in particular, precipitates, may not be completely generated, thereby leading to an inability to improve hydrogen delayed fracture resistance.
  • nickel (Ni) is included in an amount exceeding 0.1 wt%, the amount of the remaining austenite may be increased to degrade impact toughness and manufacturing costs may be increased due to an excessive amount of nickel.
  • Lanthanum (La) is included in the wire rod in an amount of 30 to 70 ppm.
  • Lanthanum (La) may be a very important element forming a compound within a grain boundary, together with Nickel (Ni) and decreasing phosphorous and sulfur segregated in the grain boundary.
  • Ni Nickel
  • lanthanum (La) is included in an amount less than 30ppm, the compound may not be effectively formed and the removal of phosphorus and sulfur segregated in the grain boundary may not be facilitated.
  • the securing of tensile strength may be enabled but superior hydrogen delayed fracture resistance may not be expected.
  • the upper limit of the amount of added lanthanum may be 70ppm.
  • the balance of the composition is iron (Fe) and inevitable impurities.
  • the wire rod according to the exemplary embodiment of the present invention includes a lanthanum (La)-based, a nickel (Ni)-based, or a LaNi-based precipitate.
  • Types of the precipitate are not particularly limited, and examples thereof may include LaNi 5 , LaPO 4 , La 2 O 2 S.
  • the precipitate may be formed in a grain or a grain boundary of a microstructure and trap hydrogen introduced into the grain or the grain boundary to prevent the introduced hydrogen from deteriorating strength of the grain boundary, thereby improving hydrogen delayed fracture resistance.
  • FIG. 1 schematically illustrates a state in which precipitates are distributed by observing the microstructure of the wire rod according to the exemplary embodiment of the present disclosure. As illustrated in FIG. 1 , it may be confirmed that precipitates of LaNi 5 , LaPO 4 , and La 2 O 2 S are distributed in a grain or a grain boundary of the microstructure, and a compound of LaNi 5 H 6 is present due to the trapping of hydrogen.
  • FIG. 2 schematically illustrates hydrogen trapping effects using a molybdenum (Mo) precipitate according to the related art, and the molybdenum (Mo) precipitate may be intended to trap introduced hydrogen within an interface between the precipitate and a grain to thereby improve hydrogen delayed fracture resistance.
  • Mo molybdenum
  • the precipitate according to the exemplary embodiment of the present disclosure may allow for the formation of a compound (for example, LaNi 5 H 6 ) including introduced hydrogen, rather than confining the hydrogen to a surface of the precipitate, such that hydrogen present in steel may be completely confined to thereby improve hydrogen delayed fracture resistance.
  • a defect in which hydrogen is separated from the surface of the precipitate may be present, but such a defect may be fundamentally extinct, such that superior hydrogen delayed fracture resistance may be obtained, in the embodiment of the present disclosure.
  • FIG. 4 illustrates a crystal structure of LaNi 5 H 6 of FIG. 3 , and it can be confirmed that the compound of LaNi 5 H 6 may have a structure capable of storing a considerable amount of hydrogen therein.
  • the aspect ratio of the precipitate is 1.2 to 2.0.
  • the aspect ratio of the precipitate is less than 1.2, the securing of the compound may rarely be allowed due to the crystal structure.
  • the aspect ratio of the precipitate exceeds 2.0, the precipitate may be easily broken.
  • continuity thereof with a base may be deficient and micro-voids may be generated, thereby causing defects.
  • breakage of the wire rod may be caused and expected hydrogen delayed fracture resistance may not be secured.
  • a circular-equivalent diameter of the precipitate may be 100 to 400nm.
  • the diameter is less than 100nm, the size of the precipitate may be excessively small, an amount of hydrogen trapped in the precipitate may be reduced, whereby effective hydrogen trapping effects may not be secured.
  • the diameter exceeds 400nm, and is significantly large, since the number of precipitates distributed per unit area may be reduced, a decrease in a surface area of the precipitates in the overall steel may result, thereby reducing hydrogen trapping effects, the upper limit of the diameter of the precipitate may be 400 nm.
  • steel satisfying the composition described above is heated to a temperature of Ae3+150°C to Ae3+250°C.
  • the heating to the temperature may be intended to maintain an austenite single phase, and in a range of the temperature, austenite grain coarsening may not be generated and the remaining segregation, carbides and inclusions may be effectively dissolved.
  • the temperature exceeds Ae3+250°C, an austenite grain may be significantly coarse, such that a final microstructure formed after cooling may be highly coarse, resulting in an inability to secure a high strength wire rod having a high degree of toughness.
  • the heating temperature is less than Ae3+150°C, heating effects may not be obtained and consequently, the heating temperature is Ae3+150°C to Ae3+250°C.
  • the heating may be undertaken for 30 minutes to one and a half hours. When the heating is performed for less than 30 minutes, the entire temperature may not be uniform. When the heating is performed for more than one and a half hours, possibility that the austenite grain may be coarse may be higher and productivity may be significantly reduced.
  • the heated steel is cooled and is subjected to hot rolling.
  • the cooling is performed at a cooling rate of 5 to 15°C/s and the rolling is performed at a temperature of Ae3+50°C to Ae3+150°C, to thereby manufacture a wire rod.
  • the cooling may be intended to perform controlling aiming at minimizing the transformation of the microstructure.
  • productivity may be decreased, an additional device may be required in order to maintain a slow cooling rate, and further, strength and toughness of the wire rod may be deteriorated after the hot rolling, similarly to the case in which the heating is maintained for long hours.
  • the cooling rate exceeds 15°C/s, since driving force of the transformation in steel before the rolling may be increased, the possibility that a new microstructure may emerge during the rolling may be increased, such that a lower rolling temperature may need to be reset.
  • the rolling temperature may be a temperature at which the emergence of a microstructure caused by the transformation during the rolling may be inhibited, recrystallization may not be generated, and only sizing rolling may be enabled.
  • the rolling temperature is less than Ae3+50°C, it may be close to the dynamic recrystallization temperature, such that the securing of the microstructure may be unavailable and general soft ferrite may be highly secured.
  • the rolling temperature is greater than Ae3+150°C, since reheating may be required after the cooling, the upper limit of the rolling temperature may be set as described above.
  • the wire rod manufactured through the rolling as described above is cooled to 600 °C or less at a cooling rate of 0.5 to 3°C/s.
  • the cooling rate may refer to a cooling rate at which the diffusion of carbon may be suppressed by the addition of manganese, and the wire rod may be effectively generated while pearlite is incompletely generated and a sufficient area fraction is secured.
  • the cooling rate is less than 0.5°C/s, the cooling rate may be extremely low, thereby degrading productivity to a degree to which actual work becomes infeasible.
  • the cooling rate exceeds 3°C/s hardenability may be improved due to overlapping effects of the added elements, such that ferrite-pearlite transformation may be delayed and a low temperature structure such as martensite or bainite may be generated.
  • the bolt manufactured using the wire rod according to the embodiment of the present disclosure may have ultrahigh strength and at the same time, may have superior hydrogen delayed fracture resistance due to the precipitate.
  • the bolt according to the exemplary embodiment of the present disclosure has an ultrahigh strength of 1200 MPa or greater and at the same time, ⁇ superior hydrogen delayed fracture resistance.
  • the manufacturing method of a wire rod having tensile strength of 1200 MPa or greater may be performed according to the following operations.
  • bolt-forming is performed using the wire rod according to the embodiment of the present disclosure, and a heat treatment is performed on the formed bolt at a temperature of 850 to 950°C.
  • the heat treatment may be intended to achieve homogenization of the structure through austenizing.
  • the temperature is less than 850°C, a sufficient amount of homogenization may not be performed, while when the temperature is greater than 950°C, no further effects derived from an increase in temperature may be secured and ductility may be deteriorated due to the coarsening of grains.
  • the upper limit of the temperature is 950°C.
  • the structure homogenized through rapid cooling may form a low temperature transformation structure such as a martensite structure to thereby improve strength of the bolt.
  • the tempering is intended to control strength and improve brittleness by removing residual stress generated due to the rapid cooling.
  • the temperature is less than 300°C, sufficient removal of residual stress may be difficult and rather, brittleness may be generated as a temper brittleness phenomenon.
  • the temperature is 300°C or greater.
  • the temperature exceeds 500°C, the strength may be reduced due to an excessive heat treatment, thereby leading to an inability to secure a required level of strength.
  • the tempering is undertaken at a temperature of 300 to 500°C.
  • the method for manufacturing the bolt may be intended to secure a required level of strength by applying a common heat treatment thereto.
  • the common heat treatment may be applied by controlling time and temperature in order to secure strength required by a person having ordinary skill in the art and the present disclosure is not particularly limited thereto.
  • Comparative examples 9 and 11 have sufficient strength and hydrogen delayed fracture resistance, but are not preferable in terms of economical feasibility due to the addition of an excessive amount of La and Ni, respectively.

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  • Organic Chemistry (AREA)
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Claims (10)

  1. Walzdraht mit hervorragender wasserstoffverzögerter Bruchfestigkeit und mit einer Zusammensetzung bestehend aus C: 0,3 bis 0,7 Gew.-%, Si: 0,05 bis 2,0 Gew.-%, Mn: 0,7 bis 1,5 Gew.-%, La: 30 bis 70 ppm, Ni: 0,01 bis 0,1%, wobei es sich bei dem Rest um Fe und unvermeidbare Verunreinigungen handelt,
    wobei der Walzdraht ein Präzipitat auf Lanthan-(La)-Basis, Nickel-(Ni)-Basis oder LaNi-Basis enthält,
    wobei das Seitenverhältnis des Präzipitats 1,2 zu 2,0 beträgt.
  2. Walzdraht nach Anspruch 1, wobei ein mittlerer kreisformäquivalenter Durchmesser des Präzipitats 100 bis 400 nm beträgt.
  3. Walzdraht nach Anspruch 1 oder 2, wobei es sich bei dem Präzipitat um LaNi5 und/oder LaPO4 und/oder La2O2S handelt.
  4. Verfahren zum Herstellen eines Walzdrahts mit hervorragender wasserstoffverzögerter Bruchfestigkeit, wobei das Verfahren umfasst:
    Erhitzen eines Stahls, der eine Zusammensetzung hat, die aus C: 0,3 bis 0,7 Gew.-%, Si: 0,05 bis 2,0 Gew.-%, Mn: 0,7 bis 1,5 Gew.-%, La: 30 bis 70 ppm, Ni: 0,01 bis 0,1% besteht, wobei es sich bei dem Rest um Fe und unvermeidbare Verunreinigungen handelt, auf eine Temperatur von Ae3+150°C bis Ae3+250°C;
    Abkühlen des erhitzten Stahls mit einer Rate von 5 bis 15°C/s, und Walzen des Stahls bei einer Temperatur von Ae3+50°C bis Ae3+150°C, um einen Walzdraht herzustellen; und
    Abkühlen des gewalzten Walzdrahts auf 600°C oder darunter mit einer Rate von 0,5 bis 3°C/s, wobei sich ein Präzipitat auf Lanthan-(La)-Basis, Nickel-(Ni)-Basis oder LaNi-Basis bildet, wobei das Seitenverhältnis des Präzipitats 1,2 zu 2,0 beträgt.
  5. Verfahren nach Anspruch 4, wobei das Erhitzen 30 Minuten bis eineinhalb Stunden lang erfolgt.
  6. Schraube, die eine Zusammensetzung, die aus C: 0,3 bis 0,7 Gew.-%, Si: 0,05 bis 2,0 Gew.-%, Mn: 0,7 bis 1,5 Gew.-%, La: 30 bis 70 ppm, Ni: 0,01 bis 0,1% besteht, wobei es sich bei dem Rest um Fe und unvermeidbare Verunreinigungen handelt, und eine Zugfestigkeit von 1200 MPa oder höher und eine hervorragende wasserstoffverzögerte Bruchfestigkeit hat,
    wobei eine Mikrostruktur der Schraube ein Präzipitat auf Lanthan-(La)-Basis, Nickel-(Ni)-Basis oder LaNi-Basis mit einem Seitenverhältnis von 1,2 zu 2,0 enthält.
  7. Schraube nach Anspruch 6, wobei ein mittlerer kreisformäquivalenter Durchmesser des Präzipitats 100 bis 400 nm beträgt.
  8. Schraube nach Anspruch 6 oder 7, wobei es sich bei dem Präzipitat um LaNiS und/oder LaP04 und/oder La2O2S handelt.
  9. Verfahren zum Herstellen einer Schraube mit einer Zugfestigkeit von 1200 MPa oder höher und einer hervorragenden wasserstoffverzögerten Bruchfestigkeit, wobei das Verfahren umfasst:
    Erhitzen eines Stahls, der eine Zusammensetzung hat, die aus C: 0,3 bis 0,7 Gew.-%, Si: 0,05 bis 2,0 Gew.-%, Mn: 0,7 bis 1,5 Gew.-%, La: 30 bis 70 ppm, Ni: 0,01 bis 0,1% besteht, wobei es sich bei dem Rest um Fe und unvermeidbare Verunreinigungen handelt, auf eine Temperatur von Ae3+150°C bis Ae3+250°C;
    Abkühlen des erhitzten Stahls mit einer Rate von 5 bis 15°C/s, und Walzen des Stahls bei einer Temperatur von Ae3+50°C bis Ae3+150°C, um einen Walzdraht herzustellen; und
    Abkühlen des gewalzten Walzdrahts auf 600°C oder darunter mit einer Rate von 0,5 bis 3°C/s, wobei sich ein Präzipitat auf Lanthan-(La)-Basis, Nickel-(Ni)-Basis oder LaNi-Basis mit einem Seitenverhältnis von 1,2 zu 2,0 bildet; und
    Ausbilden der Schraube unter Verwendung des abgekühlten Walzdrahts; Durchführen einer Hitzebehandlung an der ausgebildeten Schraube bei einer Temperatur von 850 bis 950°C; und
    Durchführen einer Abschreckung nach der Wärmebehandlung, und dann durchführen einer Temperung bei einer Temperatur von 300 bis 500°C.
  10. Verfahren nach Anspruch 9, wobei das Erhitzen 30 Minuten bis eineinhalb Stunden lang erfolgt.
EP12814354.2A 2011-07-15 2012-05-14 Walzdraht mit hervorragender wasserstoffverzögerter bruchfestigkeit, herstellungsverfahren dafür, hochfester schraubbolzen damit und verfahren zur herstellung des bolzens Not-in-force EP2733229B9 (de)

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KR1020110070206A KR101325317B1 (ko) 2011-07-15 2011-07-15 수소지연파괴 저항성이 우수한 선재와 그 제조방법 및 이를 이용한 고강도 볼트와 그 제조방법
PCT/KR2012/003757 WO2013012161A1 (ko) 2011-07-15 2012-05-14 수소지연파괴 저항성이 우수한 선재와 그 제조방법 및 이를 이용한 고강도 볼트와 그 제조방법

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CN103820726A (zh) * 2014-03-17 2014-05-28 河南赛诺米特种设备有限公司 一种疲劳强度较高螺栓的制造方法
JP6601284B2 (ja) * 2016-03-11 2019-11-06 日本製鉄株式会社 高強度ボルト
US11572612B2 (en) 2017-12-11 2023-02-07 Korea Institute Of Materials Science High-entropy alloy, and method for producing the same
US20230127592A1 (en) 2020-03-27 2023-04-27 Motp Llc Steel material and method for producing same

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EP2733229A1 (de) 2014-05-21
EP2733229A4 (de) 2015-04-08
EP2733229B9 (de) 2016-07-13
KR101325317B1 (ko) 2013-11-08
WO2013012161A1 (ko) 2013-01-24
JP2014525987A (ja) 2014-10-02
US20140150934A1 (en) 2014-06-05
CN103649354B (zh) 2016-07-06
JP5826383B2 (ja) 2015-12-02
CN103649354A (zh) 2014-03-19

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