WO2009087990A1 - Tôle d'acier résistante à l'usure présentant une excellente résistance à l'usure à haute température et une excellente aptitude à la transformation lors du pliage et procédé pour la production de celle-ci - Google Patents

Tôle d'acier résistante à l'usure présentant une excellente résistance à l'usure à haute température et une excellente aptitude à la transformation lors du pliage et procédé pour la production de celle-ci Download PDF

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WO2009087990A1
WO2009087990A1 PCT/JP2009/050024 JP2009050024W WO2009087990A1 WO 2009087990 A1 WO2009087990 A1 WO 2009087990A1 JP 2009050024 W JP2009050024 W JP 2009050024W WO 2009087990 A1 WO2009087990 A1 WO 2009087990A1
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wear
wear resistance
temperature
resistant steel
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PCT/JP2009/050024
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English (en)
Japanese (ja)
Inventor
Tatsuya Kumagai
Naoki Saitoh
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Nippon Steel Corporation
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Application filed by Nippon Steel Corporation filed Critical Nippon Steel Corporation
Priority to JP2009509198A priority Critical patent/JP4590012B2/ja
Priority to AU2009203476A priority patent/AU2009203476B2/en
Priority to EP09700890.8A priority patent/EP2180076B1/fr
Priority to CN2009800000615A priority patent/CN101680071B/zh
Priority to BRPI0901014-9A priority patent/BRPI0901014A2/pt
Priority to US12/532,032 priority patent/US20100139820A1/en
Publication of WO2009087990A1 publication Critical patent/WO2009087990A1/fr

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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
    • 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
    • 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
    • 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
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • 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

Definitions

  • the present invention relates to a wear-resistant steel plate excellent in high-temperature wear resistance and bending workability used for construction machinery and industrial machinery, and a method for producing the same.
  • wear resistant steel of the HB500 class (with a Brinell hardness of about 450 to 550 at room temperature) is excellent in wear resistance but not very good in bending workability.
  • Wear resistant steel of HB400 class (with Brinell hardness of about 360 to 440 at room temperature) with lower hardness can be bent relatively easily, and is applied to many parts that require processing. Abrasion resistance, particularly in high temperature environments, is not sufficient.
  • steel sheets for wear-resistant applications do not require a particularly high toughness value, but a certain toughness value is set so that cracks do not occur even if the thickness of the steel sheet decreases during use. It is necessary to have. Even considering use in cold regions, it is considered that Charpy absorbed energy at ⁇ 40 ° C. is 27 J or more.
  • Patent Document 1 as a wear-resistant steel for high-temperature applications of Brinell hardness HB500 class.
  • the invention described in this document is designed with the highest priority on high temperature wear resistance, and does not take any special measures to improve the bending workability, and is therefore limited to applications where the bending radius is relatively gentle. .
  • Patent Document 2 relates to wear resistant steel for medium and normal temperatures used in a region where the temperature is changed from 300 ° C to 400 ° C.
  • toughness and workability are not taken into consideration and their characteristics are not shown, but because Si is very high, toughness is not high and workability is not high.
  • Patent Document 3 relates to HB400 class wear-resistant steel having excellent bending workability, but no consideration is given to wear resistance in a high-temperature environment.
  • the HB400 class wear-resistant steel having good bending workability and the wear-resistant steel plate having high wear resistance even in a high temperature environment from 300 ° C. to 400 ° C. are suitable so far. I can't find it.
  • the wear-resistant steel plate is a consumable item, economic efficiency is also an important factor, and it is desirable that the amount of expensive alloy elements added be as low as possible.
  • the present invention is a wear-resistant steel that is HB400 class room temperature hardness with good bending workability and has high wear resistance even in a high temperature environment of 300 ° C. to 400 ° C., and is also excellent in economy.
  • the purpose is to provide.
  • the present invention assumes a high temperature environment of 300 ° C. to 400 ° C., but the typical temperature for characteristic evaluation is set to 350 ° C., and the martensitic steel having various chemical compositions at 350 ° C.
  • the wear resistance was investigated.
  • the abrasion resistance evaluation was performed as follows. In a pin-on-disk type wear test device compliant with ASTM G99-05, the sample temperature is controlled so that the sample temperature is 350 ° C., and the wear amount of the test sample and the standard sample (SS400) is determined. It was measured. Then, using SS400 as a standard sample, [wear amount of SS400 / wear amount of test sample] was defined as a 350 ° C. wear resistance ratio, and this 350 ° C. wear resistance ratio was determined. It can be said that the larger this value, the better the wear resistance at 350 ° C.
  • FIG. 1 shows 0.15% C-0.57% Si-0.41% Mn-1.37% Cr-0.08% Mo-0.012% Ti-0.0011% B-0.0032% This is the relationship between the Nb addition amount and the 350 ° C. wear resistance ratio of martensitic steel with N as the basic composition and the Nb amount varied.
  • the Nb addition amount is 0 to 0.03%, the 350 ° C. wear resistance ratio does not change much, but when the Nb addition amount exceeds 0.03%, the 350 ° C. wear resistance ratio is greatly improved.
  • Nb carbonitride precipitated during rolling suppresses recrystallization and refines the structure, Nb is usually added in an amount of 0.01 to 0.02% for this purpose.
  • Nb carbonitride deposited during rolling does not contribute much to high temperature hardness.
  • Nb existing in a solid solution state in the steel sheet remains in a solid solution state at 300 ° C. to 400 ° C. or exists as a very fine carbonitride, and any of them contributes to an improvement in high temperature hardness. Inferred. That is, when the steel sheet is heated to 350 ° C. by adding Nb in an amount that greatly exceeds the amount precipitated during rolling and by increasing the solid solution Nb in the steel sheet by selecting appropriate rolling and cooling conditions. It is considered that the hardness can be increased, and as a result, the 350 ° C. wear resistance can be improved.
  • the inventors have analyzed in detail the relationship between the alloying elements and the 350 ° C. wear resistance of a larger number of martensitic steels having an HB in the range of 360 to 440 at 25 ° C. As a result, the following formula (1) for predicting the 350 ° C. wear resistance ratio from the chemical composition was derived.
  • FIG. 2 shows the relationship between HI and the 350 ° C. wear resistance ratio of martensitic steel.
  • the target value of the high temperature wear resistance in the present invention is set such that the 350 ° C. wear resistance ratio is 3.0 or more, that is, the wear loss is 1/3 or less of SS400.
  • HI should be 0.7 or more.
  • the wear resistance ratio is 4.0 or more, and a better wear resistance can be obtained.
  • the applied plate thickness of wear-resistant steel is often up to 50 mm. If the following Ceq is more than 0.50, it is possible to ensure hardenability sufficient to obtain a martensite structure up to the center of a steel plate having a thickness of 50 mm.
  • Ceq [C] + [Si] / 24 + [Mn] / 6 + [Ni] / 40 + [Cr] / 5 + [Mo] / 4 + [V] / 14
  • [C], [Si], [Mn], [Ni], [Cr], [Mo], and [V] contain C, Si, Mn, Ni, Cr, Mo, and V, respectively. Amount (% by mass).
  • the wear-resistant steel sheet having excellent high-temperature wear resistance and bending workability according to the present invention is in mass%, C: 0.13% or more, 0.18% or less, Si: 0.5% or more, 1.0 %, Mn: 0.2% or more, 0.8% or less, P: 0.020% or less, S: 0.010% or less, Cr: 0.5% or more, 2.0% or less, Mo: 0 0.03% or more, 0.30% or less, Nb: more than 0.03%, 0.10% or less, Al: 0.01% or more, 0.20% or less, B: 0.0005% or more, 0.0030 %, N: 0.010% or less, Fe and unavoidable impurities as the balance, the composition of the following HI is 0.7 or more, and Ceq is more than 0.50 And HB (Brinell hardness) is 360 or more and 440 or less at 25 ° C.
  • the method for producing a wear-resistant steel sheet having excellent high-temperature wear resistance and bending workability comprises heating a steel slab or slab having the composition described in (1) or (2) above 1200 ° C.
  • the hot rolling is performed at a cumulative reduction ratio of 30% or more and 65% or less at 960 ° C. or lower and 900 ° C. or higher, and the hot rolling is finished at 900 ° C. or higher.
  • the present invention has HB400 class room temperature hardness with good bending workability, and has high wear resistance even in a high temperature environment from 300 ° C. to 400 ° C., and is also excellent in economic efficiency.
  • a wear-resistant steel plate can be easily manufactured.
  • FIG. 1 is a graph showing the relationship between the amount of Nb added and the wear resistance at 350.degree.
  • FIG. 2 is a graph showing the relationship between HI and wear resistance at 350 ° C.
  • C is an important element that determines the hardness of martensite.
  • the C range is 0.13% or more and 0.18% or less in order to set the room temperature HB at the center of the plate thickness up to 50 mm to 360 to 440.
  • Si is an element particularly effective for improving the 350 ° C. wear resistance, and the alloy price is also low.
  • addition of a large amount of Si reduces toughness and processability.
  • the Si addition amount is set to 0.50% or more and less than 1.0%. In the case where workability is more important, the Si addition amount is desirably less than 0.8%.
  • Mn is essential in order to avoid a decrease in toughness and bending workability due to segregation of grain boundaries of S by forming MnS, and 0.2% or more is added. Since Mn improves hardenability, it is better to add Mn in order to ensure the normal temperature hardness at the center of the plate thickness up to 50 mm. However, on the other hand, Mn lowers the high-temperature strength, so it rather lowers the 350 ° C. wear resistance. For this reason, the amount of Mn added is desirably less than 0.5%. For the purpose of improving hardenability, the upper limit is made 0.8%. Therefore, the amount of Mn added is 0.2% or more and 0.8% or less, desirably 0.2% or more and less than 0.5%.
  • P P is an inevitable impurity and is a harmful element that reduces bending workability and toughness. Therefore, the content is suppressed to 0.020% or less. More desirably, the content is 0.010% or less.
  • P is preferably as low as possible for bending workability and toughness, but an increase in refining cost is inevitable in order to reduce it to less than 0.0005%. Therefore, it is necessary to limit P to such a very low level. Absent.
  • S is also an inevitable impurity and is a harmful element that reduces bending workability and toughness. Therefore, the content is suppressed to 0.010% or less. More preferably, it is made 0.005% or less. S is preferably as low as possible for bending workability and toughness, but an increase in refining cost is inevitable in order to reduce it to less than 0.0005%, so it is necessary to limit it to such a very low level. Absent.
  • Cr is effective in improving hardenability and improving 350 ° C. wear resistance, so is added at least 0.5% or more.
  • the addition amount is desirably 1.0% or more.
  • the toughness may be lowered, so the content is made 2.0% or less.
  • Mo improves the wear resistance at 350 ° C. and, in the presence of Nb, has the effect of greatly increasing the hardenability by adding a small amount. Therefore, addition of 0.03% or more is essential. However, if excessively added, the toughness may be lowered, so the upper limit of the amount of Mo added is 0.30%. Moreover, Mo is very expensive in recent years, and the addition amount is preferably less than 0.10% from the viewpoint of suppressing alloy costs.
  • Nb is very effective in improving the 350 ° C. wear resistance because it exists in a solid solution state in the steel sheet.
  • the amount of Nb added to ensure sufficient solute Nb is more than 0.03%, and more preferably 0.04% or more.
  • Nb (CN) may not be sufficiently dissolved at the time of heating if the amount of Nb is large. Such undissolved Nb does not contribute to improving the high temperature hardness and may cause a decrease in toughness. Therefore, the Nb addition amount is set to 0.10% or less, and more desirably 0.08% or less.
  • Al is added in an amount of 0.01% or more as a deoxidation element or inclusion form control element. Moreover, in order to secure the free B necessary for improving the hardenability, 0.05% or more is added for the purpose of fixing N. In either case, excessive addition may reduce toughness, so the upper limit is made 0.20%, preferably 0.10%.
  • B is an essential element that is very effective for improving hardenability. In order to exert the effect, 0.0005% or more is necessary, but if added over 0.0030%, weldability and toughness may be lowered, so the B content is 0.0005% or more, 0 0030% or less.
  • N When N is excessively contained, the toughness is reduced, and BN is formed to inhibit the effect of improving the hardenability of B, so the content is suppressed to 0.010% or less. More desirably, it is 0.006% or less. N is preferably as low as possible in order to avoid toughness and BN formation, but in order to reduce it to less than 0.001%, an increase in refining cost is inevitable, so it is necessary to limit to such a very low level. Absent.
  • Cu is an element that can improve hardness without reducing toughness, and may be added in an amount of 0.05% or more for that purpose. However, if too much Cu is added, the toughness may be lowered, so the addition amount is 1.5% or less.
  • Ni is an effective element for improving toughness, and 0.05% or more may be added for the purpose. However, since Ni is an expensive element, the addition is made 1.0% or less.
  • V is an element effective for improving the 350 ° C. wear resistance. For this purpose, 0.01% or more may be added. However, V is also an expensive element, and if added excessively, the toughness may be lowered. Therefore, even when added, the content is made 0.20% or less.
  • Ti may be added so as to prevent formation of BN by fixing N as TiN and to secure free B necessary for improving hardenability. For this purpose, 0.003% or more is added. Added. However, the addition of Ti tends to lower the 350 ° C. wear resistance. Therefore, the amount of Ti added is 0.030% or less.
  • the component composition is limited so that the HI of formula (1) is 0.7 or more and Ceq is more than 0.50. However, if HI or Ceq is too high, the toughness may be lowered. Therefore, it is desirable that HI is 1.2 or less and Ceq is 0.70 or less.
  • the manufacturing method of the wear-resistant steel plate of the present invention will be described.
  • hot rolling is performed by heating a steel slab (slab) or slab having the above steel composition.
  • the method for producing a steel slab or slab prior to hot rolling is not particularly limited.
  • the components are adjusted so that the desired component content is obtained by various secondary scouring, and then, in addition to normal continuous casting, casting by ingot method, thin slab What is necessary is just to cast by methods, such as casting.
  • Scrap may be used as a raw material.
  • a slab obtained by continuous casting it may be directly sent to a hot rolling mill as it is a high-temperature slab, or may be hot-rolled after being reheated in a heating furnace after being cooled to room temperature.
  • the components of the steel slab or slab are the same as the components of the wear-resistant steel plate of the present invention described above.
  • the heating temperature of the steel slab or slab is set to 1200 ° C. or higher so that Nb is sufficiently dissolved. However, if the heating temperature is too high, the austenite structure becomes coarse, and therefore the structure after hot rolling may not be sufficiently refined and the toughness may be lowered. Therefore, the heating temperature of the steel slab or slab is 1350 ° C. or less. Is desirable.
  • the cumulative rolling reduction is set to 30% to 65% at 960 ° C. or lower and 900 ° C. or higher. In order to minimize the precipitation of Nb carbonitride during rolling, it is limited to this temperature and rolling reduction range. Further, in order to avoid unnecessary Nb carbonitride precipitation and leave a large amount of solid solution Nb, the hot rolling is finished at 900 ° C. or higher. Moreover, the end temperature of hot rolling needs to be 960 degrees C or less.
  • accelerated cooling is performed by direct quenching or reheating quenching.
  • direct quenching accelerated cooling is performed immediately after the hot rolling to a temperature of 200 ° C. or less at a cooling rate of 5 ° C./s or more (cooling rate at the center of the plate thickness).
  • reheating and quenching after completion of hot rolling, it is once cooled to a temperature of 200 ° C. or less (the cooling rate at this time is arbitrary), and then reheated to a temperature not lower than the Ac3 transformation point. Accelerated cooling to 200 ° C. or lower so that the cooling rate at the part is 5 ° C./s or higher.
  • the cooling rate in accelerated cooling after completion of hot rolling in the case of direct quenching and in accelerated cooling after reheating in the case of reheating quenching increases as the plate thickness decreases.
  • the target plate thickness is mainly assumed to be about 4.5 mm to 50 mm.
  • the cooling rate at a plate thickness of 4.5 mm may become very large, there is no particular problem, and no upper limit is set for the cooling rate.
  • Tempering heat treatment is not particularly required, but the properties of the steel sheet do not depart from the present invention even if heat treatment is performed at a temperature of 300 ° C. or lower.
  • the wear resistance ratio (SS400) is determined by performing a wear test at a sample temperature of 350 ° C. in a pin-on-disk type wear test apparatus compliant with ASTM G99-05 as described above. Wear amount / wear amount of the test sample).
  • the target value of wear resistance is an abrasion resistance ratio of 3.0 or more. Evaluation of bending workability was performed as follows.
  • the test piece JIS No. 1 was bent 180 degrees in the C direction at a bending radius (4 t) four times the plate thickness, and the outside of the curved portion was observed after the bending test. The test was accepted when no tears or other defects occurred outside the curved portion.
  • the toughness was evaluated as follows. A JIS Z 2201 No. 4 Charpy test piece was sampled perpendicularly to the rolling direction from the center of the plate thickness, and subjected to an impact test at -40 ° C. to measure the absorbed energy value. Then, the average value of the absorbed energy values of the impact test at ⁇ 40 ° C. of the three test pieces was determined. The average value of the toughness target value was set to 27 J or more. The obtained results are shown in Tables 5 and 6. In Tables 1 to 6, the underlined numerical values indicate the component values outside the present invention, those having insufficient temperature conditions and characteristics.
  • the steel plates Nos. 1 to 17 of the inventive examples in Table 5 all satisfy the above-mentioned normal temperature hardness, wear resistance at 350 ° C., bending workability, and toughness target values.
  • the normal temperature hardness is 350 ° C.
  • One or more of the wear resistance, bending workability, and toughness of the steel is less than the target value.
  • the comparative steel plates Nos. 41 to 44 which are steel components of the present invention but deviate from the production method of the present invention, among the normal temperature hardness, wear resistance at 350 ° C., bending workability, and toughness One or more are rejected.
  • a wear-resistant steel sheet having HB400 class room temperature hardness with good bending workability, high wear resistance even in a high temperature environment of 300 ° C. to 400 ° C., and excellent in economic efficiency. Can be easily manufactured. For this reason, it is suitable for components such as bulldozer buckets that generate frictional heat due to strong impacts and sintered coke hoppers that collide with high-temperature objects, such as construction machinery and industrial machinery that require high wear resistance in high-temperature environments. Available.

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  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
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Abstract

L'invention concerne une tôle d'acier résistante à l'usure comprenant les composants suivants (en % en masse) : C : 0,13 à 0,18 % (inclus) ; Si : 0,5 % ou plus mais moins de 1,0 % ; Mn : 0,2 à 0,8 % (inclus) ; P : 0,020 % ou moins ; S : 0,010 % ou moins ; Cr : 0,5 à 2,0 % (inclus) ; Mo : 0,03 à 0,30 % (inclus) ; Nb : plus de 0,03 % et pas plus de 0,10 % ; Al : 0,01 à 0,20 % (inclus) ; B : 0,0005 à 0,0030 % (inclus) ; et N : 0,010 % ou moins, le reste étant Fe et des impuretés inévitables. La composition chimique satisfait aux exigences en ce que la valeur de HI est supérieure ou égale à 0,7 et la valeur de Ceq est supérieure à 0,50. La tôle d'acier a une valeur de HB (dureté Brinell) de 360 à 440 (inclus) à 25 °C.
PCT/JP2009/050024 2008-01-07 2009-01-06 Tôle d'acier résistante à l'usure présentant une excellente résistance à l'usure à haute température et une excellente aptitude à la transformation lors du pliage et procédé pour la production de celle-ci WO2009087990A1 (fr)

Priority Applications (6)

Application Number Priority Date Filing Date Title
JP2009509198A JP4590012B2 (ja) 2008-01-07 2009-01-06 高温耐摩耗性および曲げ加工性に優れる耐摩耗鋼板およびその製造方法
AU2009203476A AU2009203476B2 (en) 2008-01-07 2009-01-06 Wear-resistant steel plate having excellent wear resistance at high temperatures and excellent bending workability and method for manufacturing the same
EP09700890.8A EP2180076B1 (fr) 2008-01-07 2009-01-06 Plaque d'acier résistant à l'usure ayant une excellente résistance à l'usure à une température élévée et une excellente aptitude au cintrage et procécé de fabrication de celle-ci
CN2009800000615A CN101680071B (zh) 2008-01-07 2009-01-06 高温耐磨损性和弯曲加工性优异的耐磨损钢板及其制造方法
BRPI0901014-9A BRPI0901014A2 (pt) 2008-01-07 2009-01-06 Chapa de aço resistente ao desgatste tendo excelente resistência ao desgaste a altas temperaturas e excelente capacidade de trabalho de dobramento e método para produção da mesma
US12/532,032 US20100139820A1 (en) 2008-01-07 2009-01-06 Wear-resistant steel plate having excellent wear resistance at high temperatures and excellent bending workability and method for manufacturing the same

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
JP2008000301 2008-01-07
JP2008-000301 2008-01-07
JP2008268253 2008-10-17
JP2008-268253 2008-10-17

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US (1) US20100139820A1 (fr)
EP (1) EP2180076B1 (fr)
JP (1) JP4590012B2 (fr)
KR (1) KR101033711B1 (fr)
CN (1) CN101680071B (fr)
AU (1) AU2009203476B2 (fr)
BR (1) BRPI0901014A2 (fr)
TW (1) TWI341332B (fr)
WO (1) WO2009087990A1 (fr)

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2014045553A1 (fr) * 2012-09-19 2014-03-27 Ｊｆｅスチール株式会社 Tôle d'acier résistant à l'usure qui présente une excellente ténacité à basse température et une excellente résistance à l'usure due à la corrosion
JP2018123409A (ja) * 2017-02-03 2018-08-09 Ｊｆｅスチール株式会社 耐摩耗鋼板および耐摩耗鋼板の製造方法
WO2021039021A1 (fr) * 2019-08-26 2021-03-04 Ｊｆｅスチール株式会社 Tôle d'acier mince résistante à l'abrasion, et procédé de fabrication de celle-ci

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WO2014045553A1 (fr) * 2012-09-19 2014-03-27 Ｊｆｅスチール株式会社 Tôle d'acier résistant à l'usure qui présente une excellente ténacité à basse température et une excellente résistance à l'usure due à la corrosion
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WO2021039021A1 (fr) * 2019-08-26 2021-03-04 Ｊｆｅスチール株式会社 Tôle d'acier mince résistante à l'abrasion, et procédé de fabrication de celle-ci
JP6874916B1 (ja) * 2019-08-26 2021-05-19 Ｊｆｅスチール株式会社 耐摩耗薄鋼板及びその製造方法

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BRPI0901014A2 (pt) 2015-06-23
AU2009203476B2 (en) 2010-10-07
EP2180076B1 (fr) 2016-03-30
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EP2180076A1 (fr) 2010-04-28
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