WO2012002567A1 - 溶接部の靭性と耐遅れ破壊特性に優れた耐磨耗鋼板 - Google Patents

溶接部の靭性と耐遅れ破壊特性に優れた耐磨耗鋼板 Download PDF

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WO2012002567A1
WO2012002567A1 PCT/JP2011/065416 JP2011065416W WO2012002567A1 WO 2012002567 A1 WO2012002567 A1 WO 2012002567A1 JP 2011065416 W JP2011065416 W JP 2011065416W WO 2012002567 A1 WO2012002567 A1 WO 2012002567A1
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toughness
less
wear
delayed fracture
steel
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PCT/JP2011/065416
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English (en)
French (fr)
Japanese (ja)
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植田　圭治
鈴木　伸一
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Ｊｆｅスチール株式会社
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Priority to MX2013000031A priority Critical patent/MX354630B/es
Priority to US13/806,954 priority patent/US20130216422A1/en
Priority to EP11801027.1A priority patent/EP2589676B1/en
Priority to CN2011800319242A priority patent/CN102959113A/zh
Priority to AU2011272188A priority patent/AU2011272188C1/en
Priority to RU2013103814/02A priority patent/RU2550985C2/ru
Priority to KR1020137001872A priority patent/KR20130045900A/ko
Priority to CA2801703A priority patent/CA2801703C/en
Publication of WO2012002567A1 publication Critical patent/WO2012002567A1/ja

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • 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
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • 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
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    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
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    • C22C—ALLOYS
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    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
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    • 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
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
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    • 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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with 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
    • C21D2211/008—Martensite

Definitions

  • the present invention has a thickness of 4 mm or more suitable for construction machines, industrial machines, ship building, steel pipes, civil engineering, construction, etc.
  • the present invention relates to a steel plate (abrasion resist steel plate or steel sheet), and in particular, to a material having excellent weld toughness and delayed fracture resistance.
  • wear-resistant steel plates are generally cold cracking sensitive, have poor weld toughness, and when used in welded steel structures, rocks and earth and sand. In general, it is used as a liner on the surface of a steel member that comes into contact with the steel member.
  • a dumped motor lorry vessel may be used by attaching a wear-resistant steel plate only to the surface of the vessel in contact with earth and sand after being assembled by welding using mild steel. .
  • Patent Document 1 relates to a wear-resistant steel sheet excellent in delayed fracture resistance and a method for producing the same, and in order to improve delayed fracture resistance, a low Si-low P-low S-Cr, Mo, Nb composition is used. It describes that steel containing one or more of Cu, V, Ti, B and Ca is directly quenched (also referred to as direct quenching, DQ) and tempered as necessary.
  • Patent Document 2 relates to a method of manufacturing steel and steel products with high wear resistance, and in the 0.24 to 0.3 C-Ni, Cr, Mo, B system, a parameter formula consisting of the content of these elements (parameter meter formula). ) And a martensite or martensite bainite structure containing 5 to 15% by volume of austenite, and steel with improved wear resistance is described. Further, it is described that the steel of the component is cooled at a cooling rate of 1 ° C./second or more between an austenizing temperature and 450 ° C.
  • Patent Document 3 relates to a wear-resistant steel material excellent in toughness and delayed fracture resistance, and a method for producing the same, and has a component composition that requires Cr, Ti, and B and a surface layer that is tempered martensite.
  • Patent Document 4 relates to a wear-resistant steel material excellent in toughness and delayed fracture resistance, and a method for producing the same, and a component composition in which Cr, Ti, and B are essential, a surface layer is martensite, and an internal part is martensite and lower bainite. Elongation rate of prior austenite grains expressed by the ratio of the prior austenite grain size in the rolling direction to the former austenite grain size at the center of the plate thickness in the mixed basin or lower bainite single phase structure. It is described that a steel material and steel having the component composition are directly quenched after hot rolling at 900 ° C. or less and a cumulative reduction ratio of 50% or more.
  • Patent Document 5 relates to a wear resistant steel excellent in weldability, wear resistance and corrosion resistance of a welded portion, and a method for producing the same, and uses 4 to 9 mass% of Cr as an essential element, Cu, Ni Steel that satisfies one or two of the above, satisfying the parameter formula consisting of the content of the specific component, and steel of the component composition after hot rolling at a cumulative reduction of 30% or higher at 950 ° C. or lower, and at Ac3 or higher It is described that reheating and quenching are performed.
  • the conventional wear-resistant steel sheet has a high sensitivity to cold cracking in the welded portion, and in order to prevent cold cracking, preheating and postheating are performed before and after welding. It was necessary to reduce the release of hydrogen in the steel sheet and the residual stress.
  • Patent Documents 1 and 2 do not describe improving the toughness of the welded portion in wear-resistant steel, and Patent Documents 3 and 4 also define the microstructure for the purpose of improving the toughness of the base material.
  • Patent Document 5 has examined weldability and wear resistance of welds, but is not intended to improve weld toughness, and wear resistant steel proposed in Patent Documents 1 to 5 and the like. However, it has not reached to improve both the toughness of the weld and the delayed fracture resistance. Accordingly, an object of the present invention is to provide a wear-resistant steel sheet that is excellent in toughness and delayed fracture resistance of welds without causing a decrease in productivity and an increase in manufacturing cost.
  • the weld zone toughness means the toughness of the weld heat-affected zone
  • the excellent weld zone toughness means that the toughness is particularly excellent in the bond zone and the low temperature temper embrittlement temperature range.
  • the present inventors have made various factors that determine the chemical composition, manufacturing method, and microstructure of a steel sheet in order to ensure the toughness and delayed fracture resistance of a welded part for wear-resistant steel sheets.
  • the following findings were obtained through earnest research.
  • the present invention has been made by further studying the obtained knowledge, that is, the present invention 1.
  • C 0.20 to 0.30%
  • Si 0.05 to 1.0%
  • Mn 0.40 to 1.2%
  • P 0.010% or less
  • S 0.005 % Or less
  • Cr 0.40 to 1.5%
  • Nb 0.005 to 0.025%
  • Ti 0.005 to 0.03%
  • Al 0.1% or less
  • N 0.01%
  • a weldability index (hardenability index) DI * represented by the formula (1) is 45 or more
  • the composition is composed of the balance Fe and inevitable impurities
  • the microstructure is martensite as a base phase.
  • Wear-resistant steel plate with excellent toughness and delayed fracture resistance.
  • each element symbol is a content (mass%).
  • Mo 0.05 to 1.0%
  • W 0.05 to 1.0%
  • B 0.0003 to 0.0030% in mass%
  • the steel composition further includes one or more of Cu: 1.5% or less, Ni: 2.0% or less, and V: 0.1% or less in mass% 1 or 2.
  • each element symbol is a content (mass%).
  • a wear-resistant steel sheet having excellent weld toughness and delayed fracture resistance can be obtained, greatly contributing to the improvement of manufacturing efficiency and safety at the time of steel structure production, and a remarkable industrial effect. Play.
  • the component composition and the microstructure are defined.
  • “Component Composition” In the following description, “%” is “mass%”. C: 0.20 to 0.30% C is an important element for increasing the hardness of martensite and ensuring excellent wear resistance, so that its effect is required. On the other hand, if the content exceeds 0.30%, not only the weldability is deteriorated, but also the toughness in the bond portion and the low temperature tempering region is deteriorated. For this reason, it is limited to the range of 0.20 to 0.30%. Preferably, it is 0.20 to 0.28%.
  • Si acts as a deoxidizing agent and is not only necessary for steelmaking, but also has an effect of increasing the hardness of the steel sheet by solid solution strengthening by solid solution strengthening in the steel. Furthermore, it has the effect of suppressing toughness deterioration in the temper embrittlement region of the weld heat affected zone. In order to acquire such an effect, 0.05% or more of content is required. On the other hand, if the content exceeds 1.0%, the toughness of the weld heat affected zone is remarkably deteriorated, so the content is limited to 0.05 to 1.0%. Preferably, it is 0.07 to 0.5%.
  • Mn 0.40 to 1.2% Mn has the effect of increasing the hardenability of the steel, and 0.40% or more is necessary to ensure the hardness of the base material.
  • the content exceeds 1.2%, not only the toughness, ductility and weldability of the base material deteriorate, but also the grain boundary segregation of P is promoted and the occurrence of delayed fracture is promoted. For this reason, it is limited to a range of 0.40 to 1.2%. Preferably, it is 0.40 to 1.1%.
  • P 0.010% or less
  • Cr 0.40 to 1.5% Cr is an important alloying element in the present invention, and has the effect of increasing the hardenability of steel and the effect of suppressing toughness deterioration in the temper embrittlement region of the weld heat affected zone. This is because the diffusion of C in the steel sheet is delayed due to the Cr content, and when reheated to a temperature range where low temperature temper embrittlement occurs, the change in the morphology of carbides in the martensite is suppressed. . In order to have such an effect, the content of 0.40% or more is necessary. On the other hand, when it contains exceeding 1.5%, an effect will be saturated and it will become economically disadvantageous, and weldability will fall. For this reason, it is limited to a range of 0.40 to 1.5%. Preferably, it is 0.40 to 1.2%.
  • Nb 0.005 to 0.025%
  • Nb precipitates as carbonitride, refines the microstructure of the base metal and the weld heat affected zone, fixes solid solution N, improves the toughness of the weld heat affected zone, and delays fractured (delayed) It is an important element that has the effect of suppressing the occurrence of fracture). In order to acquire such an effect, 0.005% or more needs to be contained. On the other hand, if the content exceeds 0.025%, coarse carbonitrides may precipitate, which may be the starting point of fracture. For this reason, it limits to 0.005 to 0.025% of range. Preferably, it is 0.007 to 0.023%.
  • Ti 0.005 to 0.03%
  • Ti has the effect of suppressing the coarsening of crystal grains in the bond part by fixing solid solution N and forming TiN, and toughness degradation and delayed fracture in the low temperature tempering temperature region due to the reduction of solid solution N. It has the effect of suppressing the occurrence. In order to acquire these effects, 0.005% or more needs to be contained. On the other hand, if the content exceeds 0.03%, TiC is precipitated and the base material toughness is deteriorated. For this reason, it is limited to the range of 0.005 to 0.03%. Preferably, it is 0.007 to 0.025%.
  • Al acts as a deoxidizer, and is most commonly used in the molten steel deoxidation process of steel sheets.
  • solid solution N by fixing solid solution N in steel and forming AlN, it has the effect of suppressing the coarsening of crystal grains in the bond part, and toughness deterioration and delayed fracture in the low temperature tempering temperature range due to the reduction of solid solution N It has the effect of suppressing the occurrence of.
  • the content exceeds 0.1%, it is mixed with the weld metal during welding and deteriorates the toughness of the weld metal, so the content is limited to 0.1% or less. Preferably, it is 0.01 to 0.07%.
  • N 0.01% or less N forms a nitride with Nb and Ti, and has the effect of suppressing crystal grain coarsening in the weld heat affected zone.
  • the content exceeds 0.01%, the base metal and weld toughness are remarkably lowered, so the content is limited to 0.01% or less. Preferably, it is 0.0010 to 0.0070%.
  • the balance is Fe and inevitable impurities.
  • one or more of Mo, W, B, Cu, Ni, V, REM, Ca, and Mg can be contained in addition to the basic component system.
  • Mo 0.05 to 1.0% Mo is an element that significantly increases the hardenability and is effective in increasing the hardness of the base material. In order to obtain such an effect, 0.05% or more is preferable. However, if it exceeds 1.0%, the base material toughness, ductility and weld crack resistance are adversely affected. 1.0% or less.
  • W 0.05 to 1.0% W is an element that significantly increases the hardenability and is effective in increasing the hardness of the base material. In order to obtain such an effect, the content is preferably 0.05% or more. However, if it exceeds 1.0%, the base material toughness, ductility and weld crack resistance are adversely affected. The following.
  • B 0.0003 to 0.0030%
  • B is an element that significantly increases the hardenability by adding a small amount and is effective in increasing the hardness of the base material. In order to obtain such an effect, the content is preferably 0.0003% or more. However, if it exceeds 0.0030%, the base material toughness, ductility and weld crack resistance are adversely affected.
  • Cu, Ni, and V are all elements that contribute to improving the strength of steel and can be appropriately contained depending on the desired strength.
  • Cu 1.5% or less
  • the content is preferably set to 0.1% or more. However, when the content exceeds 1.5%, the effect is saturated, and hot brittleness is generated to deteriorate the surface properties of the steel sheet. Therefore, it is made 1.5% or less.
  • Ni is an element that increases hardenability and is effective in increasing the hardness of the base material. In order to acquire such an effect, it is preferable to set it as 0.1% or more, However, if it exceeds 2.0%, since an effect will be saturated and it becomes economically disadvantageous, it shall be 2.0% or less.
  • V 0.1% or less
  • V is an element that increases the hardenability and is effective in increasing the hardness of the base material. In order to acquire such an effect, it is preferable to set it as 0.01% or more, However, If it exceeds 0.1%, in order to deteriorate a base material toughness and ductility, it is set as 0.1% or less.
  • REM, Ca, and Mg all contribute to the improvement of toughness, and are selected and added according to desired characteristics.
  • REM it is preferable to set it as 0.002% or more, but even if it exceeds 0.008%, the effect is saturated, so 0.008% is made the upper limit.
  • Ca it is preferable to make it 0.0005% or more, but since the effect is saturated even if it exceeds 0.005%, the upper limit is made 0.005%.
  • Mg it is preferable to set it as 0.001% or more, but since an effect will be saturated even if it exceeds 0.005%, 0.005% is made an upper limit.
  • DI * 33.85 ⁇ (0.1 ⁇ C) 0.5 ⁇ (0.7 ⁇ Si + 1) ⁇ (3.33 ⁇ Mn + 1) ⁇ (0.35 ⁇ Cu + 1) ⁇ (0.36 ⁇ Ni + 1) ⁇ (2.16 ⁇ Cr + 1) ⁇ (3 ⁇ Mo + 1) ⁇ (1.75 ⁇ V + 1) ⁇ (1.5 ⁇ W + 1) (1)
  • Each element symbol is a content (mass%).
  • DI * hardenability index
  • DI * hardenability index
  • the base metal base structure is martensite and wear resistance is good, but the low temperature cracking property during welding and the low temperature toughness of the welded part deteriorate. Therefore, it is preferably 180 or less. More preferably, it is in the range of 50 to 160.
  • C + Mn / 4-Cr / 3 + 10P ⁇ 0.47 Each element symbol is a content (mass%).
  • the value of this parameter: C + Mn / 4-Cr / 3 + 10P is set to 0.47 or less. Even if it exceeds 0.47, the matrix structure of the base material is martensite and has good wear resistance, but the toughness of the welded portion is significantly deteriorated. Preferably, it is 0.45 or less.
  • the base phase of the microstructure of the steel sheet (base phase or main phase) is defined as martensite. It is preferable not to mix as much as possible the structure of bainite, ferrite, or the like other than martensite because the wear resistance is reduced, but the total area ratio of these structures is 10%. If it is less, the effect can be ignored. Further, when the surface hardness of the steel plate is less than 400 HBW 10/3000 in terms of Brinell hardness, the life as a wear-resistant steel is shortened. Therefore, it is desirable that the surface hardness is 400HBW10 / 3000 or more in terms of Brinell hardness.
  • the microstructure of the bond part is a mixed structure of martensite and bainite. It is preferable not to mix as much as possible the structure such as ferrite other than martensite and bainite because the wear resistance decreases. However, if the total area fraction of these structures is less than 20%, the influence can be ignored. . Furthermore, in order to ensure the toughness of the bond part, Nb and Ti carbonitrides having an average grain size of 1 ⁇ m or less are 1000 pieces / mm 2 or more, and the average crystal grain size of prior austenite is less than 200 ⁇ m. The average grain size of the lower structure surrounded by the large tilt grain boundary having a radial hook of 15 ° or more is preferably less than 70 ⁇ m.
  • the wear-resistant steel according to the present invention can be manufactured under the following manufacturing conditions.
  • the “° C.” display relating to the temperature means a temperature at a half position of the plate thickness.
  • the molten steel having the above-described composition is melted by a known melting method to obtain a steel material such as a slab having a predetermined dimension by a continuous casting process or an ingot-bundling rolling method. preferable.
  • the obtained steel material is heated to 950 to 1250 ° C. immediately after being cooled or after being cooled, and then hot-rolled to obtain a steel plate having a desired thickness. Immediately after hot rolling, it is cooled with water or reheated for quenching. Then, tempering at 300 degrees C or less is implemented as needed.
  • the steel sheet is hot-rolled under the production conditions shown in FIG. 1 and some steel plates are water-cooled (quenched (DQ)) immediately after rolling, and the other steel plates are air-cooled after rolling, re-heated, and then water-cooled (quenched (quenched ( RQ)).
  • surface hardness measurement, wear resistance evaluation, base metal toughness measurement, T-shaped fillet weld cracking test (delayed fracture resistance evaluation), welded part reproducible thermal cycle test, and welded part toughness of actual joint The test was conducted as follows. The obtained results are shown in Table 3.
  • the abrasion resistance was in accordance with ASTM G65, and a rubber wheel test was performed.
  • the test piece is 10 mmt (t: plate thickness) x 75 mmw (w: width) x 20 mmL (L: length) (if the plate thickness is less than 10 mmt, t (plate thickness) x 75 mmw x 20 mmL) Performed using 100% SiO 2 abrasive sand.
  • the specimen weight before and after the test was measured, and the amount of wear was measured.
  • the test results were evaluated based on the wear resistance ratio: (abrasion amount of mild steel plate) / (abrasion amount of each steel plate) with the wear amount of the mild steel plate (SS400) as a reference (1.0).
  • the larger the wear resistance ratio the better the wear resistance.
  • the wear resistance ratio of 4.0 or more is excellent in wear resistance.
  • the welded heat-affected zone test simulated each of the bond and low temperature temper embrittlement regions when single layer carbon dioxide arc welding with a heat input of 17 kJ / cm was performed.
  • the bond portion was simulated at 1400 ° C. for 1 second, and a cooling rate of 800 to 200 ° C. was set to 30 ° C./s. Further, the simulation of the low temperature temper embrittlement region was held at 300 ° C. for 1 second and cooled to 300 to 100 ° C. at 5 ° C./s.
  • the average value of the three absorbed energy (vE 0 ) was determined to be 30 J or more (within the scope of the present invention) having excellent bond portion toughness.
  • Table 2 shows the production conditions of the test steel sheets, and Table 3 shows the results of the above tests.
  • Examples of the present invention (steel Nos. 1 to 5) have a surface hardness of 400 HBW 10/3000 or more, excellent wear resistance, a base metal toughness of 0 ° C. of 30 J or more, and a T-shaped fillet It was confirmed that no cracks were generated in the weld cracking test, and that excellent toughness was exhibited in the welded part thermal cycle test and the actual welded part, and the welded part toughness was excellent.
  • comparative examples (steel Nos. 6 to 14) whose composition is outside the scope of the present invention include surface hardness, wear resistance, T-shaped fillet weld cracking test, base metal toughness, reproducible thermal cycle Charpy impact test, It was confirmed that one or more of the Charpy impact test (Character impact test of actual weld joint) could not satisfy the target performance.
  • vE 0 is 30 J or more, and the absorbed energy at the test temperature of ⁇ 40 ° C. (sometimes referred to as vE- 40 ).
  • the average value of these three was determined to be 27 J or more with excellent base material toughness (within the scope of the present invention).
  • sub-size (5 mm ⁇ 10 mm) V-notch Charpy test pieces were collected, Charpy impact tests were performed, and the average value of three absorbed energy (vE 0 ) was 15 J
  • the average value of the three absorbed energy (vE- 40 ) is 13J or more as described above, and the base material toughness is excellent (within the scope of the present invention).
  • the abrasion resistance was in accordance with ASTM G65, and a rubber wheel test was performed.
  • the test piece is 10 mmt (t: plate thickness) x 75 mmw (w: width) x 20 mmL (L: length) (if the plate thickness is less than 10 mmt, t (plate thickness) x 75 mmw x 20 mmL) Performed using 100% SiO 2 wear sand.
  • the specimen weight before and after the test was measured, and the amount of wear was measured.
  • the test results were evaluated based on the wear resistance ratio: (abrasion amount of mild steel plate) / (abrasion amount of each steel plate) with the wear amount of the mild steel plate (SS400) as a reference (1.0).
  • the larger the wear resistance ratio the better the wear resistance.
  • the wear resistance ratio of 4.0 or more is excellent in wear resistance.
  • V-notch Charpy impact test was performed according to JISZ2242 (1998).
  • the V-notch Charpy impact test was conducted with test pieces at three temperatures for each steel sheet at test temperatures of 0 ° C. and ⁇ 40 ° C.
  • the average value of the three absorbed energy (vE 0 ) of the bond part and the low temperature temper embrittlement region is 30 J or more, and the average value of each three of the absorbed energy (vE ⁇ 40 ) is 27 J or more to weld toughness. Excellent (within the scope of the present invention).
  • V-notch Charpy test pieces were collected and subjected to Charpy impact tests, and the absorbed energy (vE 0 ) of the bond portion and the low-temperature temper embrittlement region ) Each having an average value of 15 J or more and an absorption energy (vE -40 ) of 13 J or more being excellent in weld joint toughness (within the scope of the present invention).
  • the V-notch Charpy impact test of the actual joint was performed with three test pieces at each test temperature with the test temperature being 0 ° C. and ⁇ 40 ° C.
  • the average value of the three absorbed energy (vE 0 ) was 30 J or more, and the average value of the three absorbed energy (vE ⁇ 40 ) was 27 J or more, which was excellent in the toughness of the bond portion (within the scope of the present invention). .
  • Table 5 shows the production conditions of the test steel sheet, and Table 6 shows the results of the above tests.
  • Examples of the present invention (steel Nos. 15 to 17 (No. 17 is a plate thickness of 8 mm)) have a surface hardness of 400 HBW 10/3000 or more, excellent wear resistance, and a base metal toughness of 0 ° C. of 30 J or more.
  • the toughness of the base metal at ⁇ 40 ° C. is 27 J or more, and further, no cracks are generated in the T-shaped fillet weld cracking test. It was confirmed that the toughness was excellent and the weld zone toughness was excellent.
  • the component composition is within the scope of the present invention, but the steel No. In the case of No. 18, surface hardness, wear resistance, base metal toughness, T-shaped fillet weld cracking test are good, but reproducible thermal cycle Charpy impact test and actual joint Charpy impact test corresponding to the low temperature temper embrittlement region. was close to the lower limit of the target performance, and it was confirmed that the low temperature toughness of the welded part was inferior to that of the other invention examples.
  • Steel No. 20 has a component composition within the range of the present invention, but since the formula (2) exceeds 0.47, both the reproduction thermal cycle Charpy impact test and the actual joint Charpy impact test have vE- 40 close to the lower limit of the performance of the present invention. It was confirmed that it was inferior to other invention examples.
  • steel No. 18 and 20 are comparative examples because the component composition is within the scope of the present invention of claim 3 but DI * and the value of formula (2) are outside the scope of the present invention of claims 6 and 7.

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PCT/JP2011/065416 2010-06-30 2011-06-29 溶接部の靭性と耐遅れ破壊特性に優れた耐磨耗鋼板 WO2012002567A1 (ja)

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MX2013000031A MX354630B (es) 2010-06-30 2011-06-29 Placa o plancha de acero resistente a la abrasión con excelente tenacidad de soldadura y resistencia a la fractura retardada.
US13/806,954 US20130216422A1 (en) 2010-06-30 2011-06-29 Abrasion resistant steel plate which exhibits excellent weld toughness and excellent delayed fracture resistance
EP11801027.1A EP2589676B1 (en) 2010-06-30 2011-06-29 Abrasion-resistant steel plate or sheet with excellent weld toughness and delayed fracture resistance
CN2011800319242A CN102959113A (zh) 2010-06-30 2011-06-29 焊接部的韧性和耐延迟断裂特性优异的耐磨损钢板
AU2011272188A AU2011272188C1 (en) 2010-06-30 2011-06-29 Abrasion resistant steel plate which exhibits excellent weld toughness and excellent delayed fracture resistance
RU2013103814/02A RU2550985C2 (ru) 2010-06-30 2011-06-29 Стойкая к истиранию толстолистовая сталь, которая демонстрирует превосходную ударную вязкость сварного шва и превосходную стойкость к замедленному разрушению
KR1020137001872A KR20130045900A (ko) 2010-06-30 2011-06-29 용접부의 인성과 내지연 파괴 특성이 우수한 내마모 강판
CA2801703A CA2801703C (en) 2010-06-30 2011-06-29 Abrasion resistant steel plate which exhibits excellent weld toughness and excellent delayed fracture resistance

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CN103966524A (zh) * 2013-01-24 2014-08-06 中国石油天然气集团公司 一种抗硫化物应力开裂的油管和套管及其制造方法
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CN113512688A (zh) * 2021-07-15 2021-10-19 重庆增隆新材料科技有限公司 一种航空超高强度钢球形粉体材料及制备方法

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KR20150036798A (ko) 2012-09-19 2015-04-07 제이에프이 스틸 가부시키가이샤 저온 인성 및 내부식 마모성이 우수한 내마모 강판
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