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WO2018110850A1 - Fil machine haute résistance doté d'une résistance au choc supérieure et procédé de fabrication associé - Google Patents

Fil machine haute résistance doté d'une résistance au choc supérieure et procédé de fabrication associé Download PDF

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Publication number
WO2018110850A1
WO2018110850A1 PCT/KR2017/013391 KR2017013391W WO2018110850A1 WO 2018110850 A1 WO2018110850 A1 WO 2018110850A1 KR 2017013391 W KR2017013391 W KR 2017013391W WO 2018110850 A1 WO2018110850 A1 WO 2018110850A1
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Prior art keywords
less
wire rod
impact toughness
high strength
present
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Ceased
Application number
PCT/KR2017/013391
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English (en)
Korean (ko)
Inventor
이형직
박인규
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Posco Holdings Inc
Original Assignee
Posco Co Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Posco Co Ltd filed Critical Posco Co Ltd
Priority to CN201780076488.8A priority Critical patent/CN110062813B/zh
Priority to EP17881235.0A priority patent/EP3556885A4/fr
Priority to US16/468,115 priority patent/US20200071792A1/en
Priority to JP2019531080A priority patent/JP6806905B2/ja
Publication of WO2018110850A1 publication Critical patent/WO2018110850A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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Classifications

    • 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
    • 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
    • C21D1/26—Methods of annealing
    • C21D1/28—Normalising
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/001—Heat treatment of ferrous alloys containing Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
    • 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
    • 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
    • C21D9/54—Furnaces for treating strips or wire
    • C21D9/56—Continuous furnaces for strip or wire
    • C21D9/573—Continuous furnaces for strip or wire with cooling
    • C21D9/5732—Continuous furnaces for strip or wire with cooling of wires; of rods
    • 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
    • C21D9/54—Furnaces for treating strips or wire
    • C21D9/56—Continuous furnaces for strip or wire
    • C21D9/573—Continuous furnaces for strip or wire with cooling
    • C21D9/5735—Details
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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
    • C21D2211/001—Austenite
    • 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
    • C21D2211/002—Bainite
    • 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
    • C21D2211/005—Ferrite
    • 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 strength wire rod having excellent impact toughness and a manufacturing method thereof, and more particularly, to a high strength wire rod having excellent impact toughness which can be preferably used as a material for industrial machinery or automobiles exposed to various external load environments, and It relates to a manufacturing method.
  • the wire of ferrite or pearlite structure has a limit in securing excellent strength and impact toughness.
  • Materials with these structures generally have high impact toughness, but relatively low strength, and when cold drawn to increase strength, high strength can be obtained, but impact toughness decreases sharply in proportion to strength increase. There is this.
  • bainite or tempered martensite is generally used to achieve high strength and excellent impact toughness.
  • the bainite structure can be obtained by constant temperature heat treatment using hot rolled steel, and the temper martensite structure can be obtained by quenching and tempering heat treatment.
  • these tissues cannot be stably obtained by the usual hot rolling and continuous cooling processes alone, and thus must be subjected to such additional heat treatment using hot rolled steel.
  • wire rods that can stably obtain bainite or martensite structure using hot rolling and continuous cooling processes without additional heat treatment have not yet been developed, and thus there is a demand for wire rod development.
  • One of the various objects of the present invention is to provide a high strength wire having excellent impact toughness and a method of manufacturing the same without additional heat treatment.
  • C less than 0.05% (excluding 0%), Si: 0.05% or less (excluding 0%), Mn: 3.0 ⁇ 4.0%, P: 0.020% or less, S: 0.020% Ni: 1.0 to 3.0%, B: 0.0010 to 0.0030%, Ti: 0.010 to 0.030%, N: less than 0.0030%, Al: 0.010 to 0.050%, remainder Fe, and inevitable impurities, High-strength wire including island martensite (MA) of less than or equal to area% (including 0 area%), cornerstone ferrites of less than or equal to 2 area% (including 0 area%), and bainitic ferrite of not less than 95 area% (including 100 area%) To provide.
  • MA island martensite
  • cornerstone ferrites of less than or equal to 2 area% (including 0 area%)
  • bainitic ferrite of not less than 95 area% (including 100 area%)
  • Another aspect of the invention is, by weight, C: less than 0.05% (excluding 0%), Si: 0.05% or less (excluding 0%), Mn: 3.0-4.0%, P: 0.020% or less, S: 0.020% Reheating the steel comprising Ni: 1.0 to 3.0%, B: 0.0010 to 0.0030%, Ti: 0.010 to 0.030%, N: 0.0030%, Al: 0.010 to 0.050%, balance Fe and unavoidable impurities, Hot rolling the reheated steel to obtain a wire rod, first cooling the wire rod at a rate of 10-20 ° C./sec to Bs ° C. to (Bs + 50) ° C., and cooling the primary cooled wire rod (Bf).
  • It provides a method of producing a high-strength wire comprising the step of secondary cooling at a rate of 2 ⁇ 5 °C / sec to -50) °C to Bf °C, and the step of air cooling the secondary cooled wire.
  • the wire rod according to the present invention is excellent in strength and impact toughness, and thus can be preferably used as a material for industrial machines or automobiles exposed to various external load environments.
  • the wire rod according to the present invention can secure excellent strength and impact toughness without additional heat treatment has an advantage in terms of economics.
  • alloy component and the preferred content range of the high strength wire rod of the present invention will be described in detail. It is noted that the content of each component described below is based on weight unless otherwise specified.
  • Carbon is dissolved in steel or exists in the form of carbide or cementite, which contributes to the increase in strength of the wire rod, but it is not intentionally added in the present invention, and there is no major obstacle in securing physical properties even if carbon is not added. However, 0% is excluded in consideration of the amount inevitably added during manufacture.
  • the carbon content is controlled to less than 0.05% in consideration of this.
  • Silicon is known as a deoxidation element together with aluminum, and is known as an element which is very effective in increasing strength through solid solution strengthening of steel by solid solution in ferrite.
  • silicon is not intentionally added, and even if silicon is not added, properties are secured. There is no big obstacle. However, 0% is excluded in consideration of the amount inevitably added during manufacture.
  • the addition of silicon is very limited in the case of cold forged parts that require sufficient ductility.
  • silicon interferes with the deposition of cementite during bainite transformation, carbon tends to concentrate on austenite, so phase martensite (M / A) is easily formed.
  • the content is controlled to 0.05% or less in order to secure excellent impact toughness.
  • Manganese increases the strength of the steel and improves the hardenability to facilitate the formation of low temperature structures such as bainite or martensite at a wide range of cooling rates.
  • the manganese content is less than 3.0%, the hardenability is not sufficient, so it is difficult to stably secure the low temperature structure by the continuous cooling process after hot rolling. On the other hand, if it exceeds 4.0%, the hardenability is so high that martensite structure is obtained even at air cooling, which is not suitable.
  • Phosphorus is unavoidably contained in steel because it is unavoidably contained in the steel and segregates at grain boundaries, thereby degrading the toughness of the steel and reducing the resistance to delayed fracture.
  • the upper limit is managed at 0.020%.
  • Sulfur is unavoidably contained in steel as it is indispensable in the grain boundary, similarly to phosphorus, to reduce toughness, to form low melting point emulsions, and to inhibit hot rolling.
  • the upper limit is managed at 0.020%.
  • Nickel acts as an element to increase hardenability with manganese. This can reduce the formation of phase martensite (M / A). If the nickel content is less than 1.0%, the hardenability is insufficient, so that the effect of inhibiting the formation of phase martensite (M / A) is insignificant, and if it exceeds 3.0%, the hardenability is so high that martensite structures are not suitable. More preferably, it is contained in 1.2 to 2.8%.
  • Boron is an element that improves the hardenability, is an element that diffuses into the austenite grain boundary, suppresses the formation of ferrite during cooling, and facilitates the formation of bainite or martensite.
  • the added amount is less than 0.0010%, the effect according to the addition cannot be expected, and if it exceeds 0.0030%, the effect can not be expected to increase any more, and the grain boundary strength is lowered due to the precipitation of boron nitride at the grain boundary, resulting in hot workability. Can be reduced.
  • Titanium has the highest reactivity with nitrogen to form nitrides first.
  • titanium When titanium is added to form TiN and exhausts most of the nitrogen in the steel, it prevents the precipitation of BN so that boron is present in a soluble state, thereby improving hardenability.
  • the added amount is less than 0.010%, the effect of the addition is insufficient, and if it exceeds 0.030%, coarse nitride may be formed to deteriorate mechanical properties.
  • Nitrogen should be kept in a soluble state with boron and should not be included as much as possible in order to fully exhibit the effect of improving hardenability. It should also be limited in order not to facilitate the formation of island martensite (M / A) during bainite transformation. In the present invention, the content is controlled to less than 0.0030%.
  • Aluminum is a powerful deoxidation element that removes oxygen in steel to improve cleanliness, and also combines with nitrogen dissolved in steel to form AlN, thereby improving impact toughness. Therefore, in the present invention, aluminum is actively added, and if the content is less than 0.010%, it is difficult to expect the effect of the addition, if it exceeds 0.050% a large amount of alumina inclusions can be generated to greatly reduce the mechanical properties.
  • the rest is Fe.
  • unavoidable impurities that are not intended from the raw materials or the surrounding environment may be inevitably mixed, and thus, this cannot be excluded. Since these impurities are known to those skilled in the art, not all of them are specifically mentioned in the present specification.
  • the C, Si, Ni content is preferably controlled to satisfy the following relational formula (1).
  • carbon may deteriorate impact toughness by forming cementite or phase martensite (M / A), and silicon may deteriorate impact toughness by solid solution in steel or facilitating formation of phase martensite (M / A).
  • M / A phase martensite
  • nickel can raise hardenability and can suppress that phase-like martensite (M / A) is formed.
  • the content of Mn, Ti, N, B is preferably controlled to satisfy the following relational formula 2.
  • the more preferable range of relation 2 is 10.0 or more, and even more preferable range is 12.0 or more.
  • Manganese in the present invention increases the hardenability to help the bainitic ferrite is easily produced even when the cooling rate is relatively small. Titanium combines with nitrogen to form nitrides, allowing boron to be sufficiently dissolved in steel, thereby suppressing ferrite production and facilitating bainitic ferrite production.
  • the inventors of the present invention have been focused on this point, and as a result of repeated studies and experiments, when the content of the manganese, titanium, boron and nitrogen satisfy the relation 2, it provides a wire of the base ferrite tissue having excellent strength and impact toughness It was confirmed that it can be done.
  • the wire rod of the present invention has a fine structure of 3% or less (including 0 area%) of phase martensite (MA), 2% or less (including 0 area%) of cornerstone ferrite and 95 or more (100 area%).
  • bainite is called various terms depending on the carbon content or morphology, and is usually referred to as upper / lower bainite above medium carbon (about 0.2 to 0.45 wt%) and below 0.2%. In the low carbon range of, it is called bainitic ferrite, acicular ferrite, granular ferrite, etc. depending on the temperature range.
  • the wire rod of the present invention has a bainitic ferrite structure among them.
  • the wire rod of the present invention as described above by using the bainitic ferrite as the main structure can be secured at the same time excellent strength and impact toughness. If the conventional ferrite other than the bainitic ferrite is a main structure, it may be advantageous in terms of impact toughness, but it is not preferable because it cannot prevent a decrease in strength.
  • the higher the area fraction of the martensite phase may be advantageous in terms of the strength of the wire rod, but the impact toughness is deteriorated.
  • Cornerstone ferrite is mainly formed along the old austenite grain boundary, greatly deteriorating impact toughness. Therefore, it is preferable to control the area ratio of the cornerstone ferrite as low as possible, and as mentioned above, it manages to 2% or less in this invention.
  • the grain size of the island martensite may be 5 ⁇ m or less (excluding 0 ⁇ m). If the grain size exceeds 5 ⁇ m, the area of the interface in contact with the bainitic ferrite matrix becomes large, which may deteriorate impact toughness.
  • the grain size means the equivalent circular diameter of the particles detected by observing one cross section of the wire rod.
  • the high-strength wire of the present invention described above can be produced by various methods, the manufacturing method is not particularly limited. However, as a preferred example, it may be prepared by the following method.
  • a steel having the above-described component system is prepared and then reheated.
  • the shape of the steel is not particularly limited, but may be in the form of bloom or billet.
  • reheating temperature has a range of 950-1050 degreeC. This is to prevent grain coarsening by reheating the steel at a relatively low temperature.
  • the reheated steel is finished hot rolled to obtain a wire rod.
  • finishing hot rolling temperature has a range of 750-850 degreeC. This is to refine the austenite grains through sufficient low-temperature rolling, and finally to obtain fine bainite structure after phase transformation to improve impact toughness.
  • the wire rod is first cooled to a Bs ° C to (Bs + 50) ° C at a rate of 10 to 20 ° C / sec.
  • Bs is the temperature at which the bainite phase transformation starts on the continuous cooling curve, and in the present invention, by cooling the wire rod at a relatively high speed until just before the bainite phase transformation, actively forming the cornerstone ferrite is formed along the austenite grain boundary.
  • Bs is preferably in the temperature range of 600 ⁇ 650 °C .
  • the first cooled wire rod is secondly cooled from (Bf-50) ° C to Bf ° C at a rate of 2 to 5 ° C / sec, followed by air cooling.
  • Bf is the temperature at which the bainite phase transformation is terminated on the continuous cooling curve. If the secondary cooling end temperature exceeds Bf ° C, it is difficult to secure a sufficient amount of bainitic ferrite structure, and if it is less than Bf-50 ° C, Is sufficiently cooled and easy to handle, but productivity may be reduced.
  • the secondary cooling rate when the secondary cooling rate is less than 2 ° C / s, the formation of the cornerstone ferrite may increase.
  • the secondary cooling rate exceeds 5 ° C / s, martensite is formed in the steel, which may deteriorate strength and impact toughness.
  • the bainite phase transformation end temperature Bf was measured using a dilatometer, and varies slightly depending on the chemical composition, and showed a range of approximately 350 ⁇ 400 °C.
  • the microstructure of the wire rods thus prepared was analyzed and shown in Table 2.
  • the tensile strength and impact toughness were measured and shown in Table 2.
  • the area fraction and grain size of island martensite (MA) in the microstructure of the wire rod were measured using an image analyzer.
  • the room temperature tensile test was measured by performing a crosshead speed (crosshead speed) at a speed of 0.9mm / min to the yield point, 6mm / min thereafter.
  • the impact test was carried out at room temperature using an impact tester having an edge curvature of 2 mm and a test capacity of 500 J to strike the specimen.
  • specimens 1 to 5 satisfying both the alloy composition and the process conditions proposed by the present invention were not only tensile strength of 600MPa or more, but also excellent impact toughness of 200J or more.
  • the nickel content was lower than the range proposed by the present invention, and many MA phases were formed, and the impact toughness was inferior.
  • Specimen 7 was superior in tensile strength as the carbon content exceeded the range suggested by the present invention, but the impact toughness was inferior. This is because carbon is dissolved in the MA phase to form a stable MA phase.
  • Specimen 8 is a case in which the silicon content exceeds the range proposed by the present invention.Since the addition of silicon also increases the amount of solid solution at the base and the effect of solid solution strengthening, the MA phase also increases as the amount of addition increases, similar to carbon. Tensile strength is good, but impact toughness is inferior.
  • Specimen 9 is low in the hardenability of steel because the content of manganese and boron is less than the range proposed by the present invention. Accordingly, even if the cooling conditions proposed by the present invention are satisfied, ferrite and bainitic ferrite structures are mixed to provide tensile strength. Inferior.
  • specimen 10 the alloy composition satisfies the range proposed in the present invention, but the phase martensite and martensite are formed as the secondary cooling rate exceeds the range suggested by the present invention in the component relationship (Relationship 1) and manufacturing process.
  • the tensile strength was excellent, but the impact toughness was inferior.
  • the alloy composition satisfies the range proposed by the present invention, but as the secondary cooling rate is less than the range proposed by the present invention, the ferrite was formed and the tensile strength was inferior.
  • specimen 12 is a case where the content of titanium is less than the range proposed in the present invention, the hardening capacity is reduced because the amount of solute boron is reduced, and the amount of cementite ferrite precipitation increases when the cooling rate is small, showing that the tensile strength is lowered. Giving.
  • specimens 13 and 14 respectively, the content of manganese and nickel exceeds the range proposed in the present invention, because the relatively hardenability is too large, even when cooled at the cooling rate proposed in the invention, the martensite is generated to increase the strength, Impact toughness was inferior.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

L'invention concerne un fil machine haute résistance présentant une résistance au choc supérieure, ainsi qu'un procédé de fabrication associé. L'invention concerne plus particulièrement un fil machine haute résistance présentant une résistance au choc supérieure, pouvant être utilisé de préférence en tant que matériau pour des machines industrielles ou des automobiles exposées à divers environnements de charge externe, ainsi qu'un procédé de fabrication associé.
PCT/KR2017/013391 2016-12-13 2017-11-23 Fil machine haute résistance doté d'une résistance au choc supérieure et procédé de fabrication associé Ceased WO2018110850A1 (fr)

Priority Applications (4)

Application Number Priority Date Filing Date Title
CN201780076488.8A CN110062813B (zh) 2016-12-13 2017-11-23 具有优异冲击韧性的高强度线材及其制造方法
EP17881235.0A EP3556885A4 (fr) 2016-12-13 2017-11-23 Fil machine haute résistance doté d'une résistance au choc supérieure et procédé de fabrication associé
US16/468,115 US20200071792A1 (en) 2016-12-13 2017-11-23 High-strength wire rod having superior impact toughness and manufacturing method therefor
JP2019531080A JP6806905B2 (ja) 2016-12-13 2017-11-23 衝撃靭性に優れた高強度線材及びその製造方法

Applications Claiming Priority (2)

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KR10-2016-0169308 2016-12-13
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KR102218441B1 (ko) * 2019-10-08 2021-02-19 주식회사 포스코 비자성 고강도 선재 및 이의 제조방법
KR102321317B1 (ko) 2019-10-16 2021-11-02 주식회사 포스코 용접봉용 선재 및 이의 제조방법

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EP3556885A1 (fr) 2019-10-23
US20200071792A1 (en) 2020-03-05
KR101879068B1 (ko) 2018-07-16
CN110062813A (zh) 2019-07-26
KR20180067894A (ko) 2018-06-21
CN110062813B (zh) 2021-05-04
EP3556885A4 (fr) 2019-10-30
JP6806905B2 (ja) 2021-01-06

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