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EP2180076A1 - Abriebfestes stahlblech mit hervorragender abriebfestigkeit bei hoher temperatur und hervorragender bieg- und verarbeitbarkeit sowie herstellungsverfahren dafür - Google Patents

Abriebfestes stahlblech mit hervorragender abriebfestigkeit bei hoher temperatur und hervorragender bieg- und verarbeitbarkeit sowie herstellungsverfahren dafür Download PDF

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Publication number
EP2180076A1
EP2180076A1 EP09700890A EP09700890A EP2180076A1 EP 2180076 A1 EP2180076 A1 EP 2180076A1 EP 09700890 A EP09700890 A EP 09700890A EP 09700890 A EP09700890 A EP 09700890A EP 2180076 A1 EP2180076 A1 EP 2180076A1
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Prior art keywords
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temperature
wear
wear resistance
amount
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Application number
EP09700890A
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English (en)
French (fr)
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EP2180076A4 (de
EP2180076B1 (de
Inventor
Tatsuya Kumagai
Naoki Saitoh
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Nippon Steel Corp
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Nippon Steel Corp
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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 having excellent wear resistance at high temperatures and excellent bending workability that can be used in construction machinery and industrial machinery, and also relates to a method for manufacturing such a wear-resistant steel plate.
  • the present application claims priority on Japanese Patent Application No. 2008-000301, filed on January 7, 2008 , and Japanese Patent Application No. 2008-268253, filed on October 17, 2008 , the contents of which are incorporated herein by reference.
  • Increasing of the hardness is effective in improving the wear resistance.
  • the steel plate having high hardness when a steel plate having high hardness is subjected to bending, and particularly bending with a small bend radius, the steel plate tends to be prone to braking or cracking.
  • having a high degree of hardness for a steel plate is disadvantageous for achieving favorable bending workability.
  • the wear resistance and the bending workability are generally mutually opposing properties.
  • an HB500 class wear-resistant steel plate (with a Brinell hardness at room temperature of approximately 450 to 550) exhibits excellent wear resistance, but has relatively poor bending workability.
  • a steel having a lower degree of hardness such as an HB400 class wear-resistant steel plate (with a Brinell hardness at room temperature of approximately 360 to 440) can be subjected to bending work comparatively easily, and can therefore be applied to all manner of members that require favorable workability, but cannot exhibit totally satisfactory wear resistance, particularly in terms of the wear resistance under high-temperature conditions.
  • imparting a wear-resistant steel having an HB400 class room temperature hardness with favorable high-temperature wear resistance properties could be said to be one effective method of achieving a combination of favorable bending workability and superior wear resistance at high temperatures.
  • a wear-resistant steel plate does not generally require a particularly high toughness value, but must have a certain level of toughness to ensure that the steel does not crack even when the thickness of the steel plate decreases during use. In consideration of use within cold regions, it is generally considered that the Charpy absorption energy at -40°C should be not less than 27 J.
  • Patent Document 1 a wear-resistant steel for high-temperature applications having a Brinell hardness in the order of HB500 class.
  • the invention disclosed in this document was designed with the high-temperature wear resistance as the overriding priority, with no particular measures taken to improve the bending workability, and therefore the steel is limited to applications in which the bend radius is comparatively large.
  • Patent Document 2 relates to a wear-resistant steel for intermediate and moderate temperatures that can be used in regions of 300°C to 400°C. This document gives no consideration to toughness or workability, and no disclosure is made regarding these properties; however, because the steel includes an extremely high level of Si, it is thought that neither the toughness nor the workability would be particularly favorable.
  • Patent Document 3 relates to an HB400 class wear-resistant steel having excellent bending workability, but absolutely no consideration is given to the wear resistance under high-temperature conditions.
  • the present invention aims to provide a wear-resistant steel having a room temperature hardness in the order of HB400 class that indicates favorable bending workability, has a high degree of wear resistance even under high-temperature conditions of 300°C to 400°C, and is very economical.
  • the present invention has been developed on the assumption of high-temperature conditions of 300°C to 400°C, and a temperature of 350°C was used as a representative temperature for evaluating the properties of the steel.
  • the wear resistance at 350°C was investigated for martensite steels having a variety of different chemical compositions. These wear resistance evaluations were conducted in the manner outlined below. Namely, the temperature of the sample was controlled within a pin-on-disk wear testing apparatus prescribed in ASTM G99-05, and wear testing was conducted while the sample temperature was set to 350°C; thereby, the amounts of wear for the test sample and for a standard sample (SS400) were measured.
  • FIG. 1 illustrates the relationship between the 350°C wear resistance ratio and the added amount ofNb for a martensite steel having a basic composition including 0.15% of C, 0.57% of Si, 0.41% of Mn, 1.37% of Cr, 0.08% of Mo, 0.012% ofTi, 0.0011% of B and 0.0032% of N, and having a variable amount of Nb.
  • the added amount of Nb was within a range from 0 to 0.03%, the 350°C wear resistance ratio varies little, but once the added amount of Nb exceeds 0.03%, the 350°C wear resistance ratio increases significantly.
  • Nb carbonitrides that precipitate during rolling tend to inhibit recrystallization and reduce the size of the steel microstructure, and therefore Nb is usually added in an amount within a range from 0.01 to 0.02%.
  • Nb carbonitrides that precipitate during rolling have almost no effect on the high-temperature hardness.
  • Nb that exists within the steel plate in a solid solution state when the temperature is within a range from 300°C to 400°C, it still remains in a solid solution state or it exists as extremely fine carbonitrides, and it is surmised that either of these states will contribute to an improvement in the high-temperature hardness.
  • the reason for subtracting 0.02 from the Nb amount is to account for the amount of Nb that precipitates during rolling.
  • FIG. 2 illustrates the relationship between HI and the 350°C wear resistance ratio of the martensite steel.
  • the target value for the high-temperature wear resistance is set as a 350°C wear resistance ratio of not less than 3.0, that is, an amount of frictional wear that is 1/3 or less than that of SS400. From the relationship illustrated in FIG. 2 it is clear that in order to satisfy this target value, the HI value must be 0.7 or greater. Moreover, if the HI value is 0.8 or higher, then the wear resistance ratio is 4.0 or greater; therefore, even more favorable wear resistance can be realized.
  • the formula (1) indicates that besides Nb, increasing the added amounts of Si, Cr, Mo and V is also effective in improving the 350°C wear resistance for a martensite steel.
  • both of Mo and V are elements that have conventionally been added in large amounts to high-temperature steels; however, because recent costs for these elements are extremely high, the added amounts are preferably kept as small as possible from the viewpoint of economic viability.
  • Si and Cr are comparatively low-cost elements, and are therefore advantageous in terms of improving the 350°C wear resistance.
  • reducing the amount of Mn is actually also advantageous in terms of achieving a favorable 350°C wear resistance.
  • Ceq C + Si / 24 + Mn / 6 + Ni / 40 + Cr / 5 + Mo / 4 + V / 14 wherein [C], [Si], [Mn], [Ni], [Cr], [Mo] and [V] represent the amounts (mass %) of C, Si, Mn, Ni, Cr, Mo and V, respectively.
  • a method for manufacturing a wear-resistant steel plate having excellent wear resistance at high temperatures and excellent bending workability includes: heating a slab having the composition disclosed in (1) or (2) above to a temperature of at least 1,200°C, conducting hot rolling with a cumulative reduction ratio of not less than 30% and not more than 65% at a temperature of not more than 960°C and not less than 900°C, finishing the hot rolling at a temperature of not less than 900°C; and after completion of the hot rolling, either immediately performing accelerated cooling to a temperature of 200°C or lower such that a cooling rate within the center of the plate thickness is at least 5°C/s, or conducting cooling to a temperature of 200°C or lower, subsequently reheating to a temperature of not less than an Ac3 transformation point, and then performing accelerated cooling to a temperature of 200°C or lower such that a cooling rate within the center of the plate thickness is at least 5°C/s.
  • a wear-resistant steel plate having a room temperature hardness in the order of HB400 class that indicates favorable bending workability has a high degree of wear resistance even under high-temperature conditions of 300°C to 400°C, and is very economical can be manufactured relatively easily.
  • C is an important element in determining the hardness of the martensite.
  • the C content is set to not less than 0.13% and not more than 0.18%.
  • Si is a particularly effective element for improving the 350°C wear resistance, and is also an inexpensive alloy element.
  • the added amount of Si is set to not less than 0.50% but less than 1.0%. If particular emphasis is placed on the workability, then the added amount of Si is preferably less than 0.8%.
  • Mn by forming MnS, is essential for preventing a reduction in the toughness and a deterioration in the bending workability caused by grain boundary segregation of S, and is added in an amount of not less than 0.2%. Since Mn enhances the hardenability, it is preferable to add Mn in a large amount for the purpose of ensuring more favorable room temperature hardness within the plate thickness center portion of a plate having a thickness of up to 50 mm. However, on the other hand, Mn causes a reduction in the high-temperature strength, and actually causes a decrease in the 350°C wear resistance. For this reason, the added amount of Mn is preferably less than 0.5%. Even in terms of enhancing the hardenability, the upper limit for the Mn content is 0.8%. Accordingly, the added amount of Mn is set to not less than 0.2% and not more than 0.8%, and is preferably not less than 0.2% but less than 0.5%.
  • the P is a harmful element that causes deterioration in the bending workability and the toughness, and is incorporated as an unavoidable impurity. Accordingly, the P content is suppressed to not more than 0.020%, This amount is preferably 0.010% or lower.
  • the amount of P is preferably as low as possible in terms of the bending workability and the toughness.
  • unavoidable increases in the refining costs are required in order to reduce the P content to less than 0.0005%, there is no necessity to limit the P content to this type of extremely low level.
  • S is also a harmful element that causes deterioration in the bending workability and the toughness, and is incorporated as an unavoidable imparity. Accordingly, the S content is suppressed to not more than 0.010%. This amount is preferably 0.005% or lower. The amount of S is preferably as low as possible in terms of the bending workability and the toughness. However, since unavoidable increases in the refining costs are required in order to reduce the S content to less than 0.0005%, there is no necessity to limit the S content to this type of extremely low level.
  • Cr is effective in improving the hardenability and improving the 350°C wear resistance, and is therefore added in an amount of at least 0.5%.
  • the added amount of Cr is preferably 1.0% or greater.
  • excessive addition of Cr can cause a reduction in the toughness, and therefore the Cr content is limited to not more than 2.0%.
  • Mo improves the 350°C wear resistance, and adding a small amount in the presence ofNb produces a large improvement in the hardenability. For this reason, at least 0.03% of Mo must be added. However, excessive addition of Mo can cause a reduction in the toughness, and therefore the added amount of Mo has an upper limit of 0.30%. Further, Mo has been extremely expensive in recent years, and in terms of suppressing the alloy cost, the added amount of Mo is preferably less than 0.10%.
  • Nb due to its existence in a solid solution state within the steel plate, is extremely effective in improving the 350°C wear resistance.
  • the amount of Nb required to ensure a satisfactory amount of solid solution Nb is an amount of greater than 0.03%, and the amount is preferably 0.04% or greater.
  • Nb(CN) may not be solid-solubilized completely during heating.
  • This type of insoluble Nb does not contribute to an improvement in the high-temperature hardness, and may actually cause a reduction in the toughness. For this reason, the added amount of Nb is not more than 0.10%, and is preferably 0.08% or lower.
  • Al is added in an amount of not less than 0.01% as a deoxidizing element or element for morphology control of inclusions. Further, Al is also added in an amount of not less than 0.05% for the purpose of fixing N in order to ensure the necessary amount of free B required to improve the hardenability. In either case, excessive addition of Al can cause a reduction in the toughness, and therefore the upper limit for the Al content is 0.20%, and preferably 0.10%.
  • B is an essential element that is extremely effective in improving the hardenability. In order to ensure satisfactory manifestation of this effect, at least 0.0005% of B is necessary. However, if B is added in an amount exceeding 0.0030%, then the weldability and the toughness of the steel may deteriorate, and therefore the B content is set to not less than 0.0005% and not more than 0.0030%.
  • N is added in excess, N causes a reduction in the toughness, and also forms BN; thereby, the effect of improving hardenability that is provided by B is inhibited. As a result, the N content is suppressed to not more than 0.010%.
  • the N content is preferably 0.006% or less.
  • the amount of N is preferably as low as possible. However, since unavoidable increases in the refining costs are required in order to reduce the N content to less than 0.001%, there is no necessity to limit the N content to this type of extremely low level.
  • the above elements represent the basic components within the steel of the present invention; however, one or more of the elements Cu, Ni, V and Ti may also be added in addition to the elements described above.
  • Cu is an element that is capable of improving the hardness without reducing the toughness, and 0.05% or more of Cu may be added for this purpose. However, if Cu is added in excess, then the toughness may actually decrease, and therefore the added amount of Cu is not more than 1.5%.
  • Ni is an element that is effective in improving the toughness, and 0.05% or more of Ni may be added for this purpose. However, because Ni is an expensive element, the amount added is limited to not more than 1.0%.
  • V is an element that is effective in improving the 350°C wear resistance. An amount of 0.01% or more of V may be added for this purpose. However, V is also an expensive element and may cause a deterioration in the toughness if added in excess, and therefore if added, the amount is limited to not more than 0.20%.
  • Ti may be added to fix N as TiN; thereby, the formation ofBN is prevented. As a result, the necessary amount of free B required to improve the hardenability is ensured. An amount of 0.003% or more of Ti may be added for this purpose. However, addition of Ti tends to cause a deterioration in the 350°C wear resistance. Accordingly, the added amount of Ti is limited to not more than 0.030%.
  • the element composition of the present invention is also restricted so that the value of HI in formula (1) is not less than 0.7, and the value of Ceq is greater than 0.50.
  • HI is preferably not more than 1.2 and Ceq is preferably not more than 0.70.
  • a slab having the steel component composition described above is heated and subjected to hot rolling.
  • the method used for manufacturing the slab prior to the hot rolling there are no particular restrictions on the method used for manufacturing the slab prior to the hot rolling.
  • a component adjustment process can be conducted using any of the various secondary refining techniques to achieve the targeted amount of each element, and casting may then be conducted using a typical continuous casting method, casting by an ingot method, or casting by another method such as thin slab casting.
  • Scrap metal may be used as a raw material.
  • the high-temperature cast slab may be fed directly to the hot rolling apparatus, or may be cooled to room temperature and then reheated in a furnace before undergoing hot rolling.
  • the components within the slab are the same as the components within the wear-resistant steel plate of the present invention described above.
  • the heating temperature for the slab is 1,200°C or higher. However, if a heating temperature is too high, coarsening of the austenite structures occurs; thereby, a microstructure after hot rolling does not become sufficiently fine and a deterioration in the toughness is caused. Therefore, the heating temperature for the slab is preferably not more than 1,350°C.
  • the cumulative reduction ratio is set to not less than 30% and not more than 65% at a temperature of not more than 960°C and not less than 900°C. The temperature and the reduction ratio are restricted to these ranges so as to reduce the amount of Nb carbonitrides precipitated during rolling to a requisite minimum which is necessary for ensuring favorable grain refinement. Further, in order to suppress unnecessary precipitation of Nb carbonitrides and maximize the amount of solid solution Nb, the hot rolling is preferably finished at a temperature of not less than 900°C. Furthermore, the hot rolling finishing temperature must be not more than 960°C.
  • accelerated cooling is conducted to obtain martensite structures, either by performing direct quenching or by reheating the rolled steel and then performing quenching.
  • direct quenching after completion of the hot rolling, the rolled plate is immediately subjected to accelerated cooling to a temperature of 200°C or lower at a cooling rate of at least 5°C/s (the cooling rate within the center of the plate thickness).
  • the rolled plate is cooled once to a temperature of 200°C or lower (the cooling rate is arbitrary), subsequently reheated to a temperature of not less than the Ac3 transformation point, and then subjected to accelerated cooling to a temperature of 200°C or lower such that the cooling rate within the center of the plate thickness is at least 5°C/s.
  • the cooling rate increases as the thickness of the steel plate decreases.
  • the target plate thickness is typically assumed to be approximately within a range from 4.5 mm to 50 mm.
  • the cooling rate for a plate having a thickness of 4.5 mm may be extremely high; however, there are no particular problems associated with such a high rate, and no upper limit is specified for the cooling rate.
  • a tempering heat treatment is not particularly necessary; however, a heat treatment at a temperature of not more than 300°C does not cause the properties of the steel plate to depart from the scope of the present invention.
  • Each of these steel plates was evaluated for room temperature hardness, wear resistance at 350°C, bending workability, and toughness.
  • the room temperature hardness was evaluated by using a Brinell hardness test method (JIS Z 2243) to measure the hardness at 25°C.
  • the target value for the room temperature hardness was a value of not less than HB360 and not more than HB440.
  • the wear resistance was evaluated by conducting wear testing using a pin-on-disk wear testing apparatus prescribed in ASTM G99-05 with the temperature of the sample held at 350°C, and then determining a wear resistance ratio relative to a SS400 standard sample (amount of wear of SS400 / amount of wear of test sample).
  • the target value for the wear resistance was a wear resistance ratio of 3.0 or greater.
  • Evaluation of the bending workability was conducted in the following manner. Namely, using the method prescribed in JIS Z 2248, a JIS No. 1 test piece was subjected to a bend test to 180° in the C-direction at a bend radius of four times the plate thickness (4t), and after the bend test, the external appearance of the curved portion of the test piece was examined. The steel plate was deemed to have passed if no cracking or other defects were observed on the outside of the curved portion. Evaluation of the toughness was conducted in the manner described below. Namely, a No. 4 Charpy test piece prescribed in JIS Z 2201 was sampled from the center of the plate thickness in a direction orthogonal to the rolling direction, an impact test was performed at -40°C, and the absorption energy was measured.
  • a wear-resistant steel plate having an HB400 class room temperature hardness that indicates favorable bending workability, has a high degree of wear resistance even under high-temperature conditions of 300°C to 400°C, and is very economical can be manufactured relatively easily.
  • the present invention can be used favorably for construction machinery and industrial machinery members that require superior wear resistance under high-temperature conditions, such as bulldozer buckets in which frictional heat is generated as a result of strong impacts, and hoppers for sintered coke which are exposed to impacts with high-temperature bodies.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
EP09700890.8A 2008-01-07 2009-01-06 Abnutzungsfestes stahlblech mit hervorragender abnutzungsfestigkeit bei hoher temperatur und hervorragender biegeverarbeitbarkeit sowie herstellungsverfahren dafür. Active EP2180076B1 (de)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
JP2008000301 2008-01-07
JP2008268253 2008-10-17
PCT/JP2009/050024 WO2009087990A1 (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

Publications (3)

Publication Number Publication Date
EP2180076A1 true EP2180076A1 (de) 2010-04-28
EP2180076A4 EP2180076A4 (de) 2013-10-23
EP2180076B1 EP2180076B1 (de) 2016-03-30

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EP09700890.8A Active EP2180076B1 (de) 2008-01-07 2009-01-06 Abnutzungsfestes stahlblech mit hervorragender abnutzungsfestigkeit bei hoher temperatur und hervorragender biegeverarbeitbarkeit sowie herstellungsverfahren dafür.

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

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EP2873747A4 (de) * 2012-09-19 2015-10-28 Jfe Steel Corp Verschleissfeste stahlplatte mit hervorragender kältezähigkeit und korrosionsverschleissfestigkeit

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JP6149778B2 (ja) 2014-03-31 2017-06-21 Ｊｆｅスチール株式会社 耐摩耗性に優れた厚鋼板およびその製造方法
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CN105839001A (zh) * 2016-05-30 2016-08-10 苏州双金实业有限公司 一种具有良好加工性能的钢
CN105886903A (zh) * 2016-06-13 2016-08-24 苏州双金实业有限公司 一种具有防磨损性能的钢
KR101899686B1 (ko) * 2016-12-22 2018-10-04 주식회사 포스코 고경도 내마모강 및 이의 제조방법
JP6610575B2 (ja) * 2017-02-03 2019-11-27 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
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EP2180076A4 (de) 2013-10-23
BRPI0901014A2 (pt) 2015-06-23
WO2009087990A1 (ja) 2009-07-16
AU2009203476B2 (en) 2010-10-07
AU2009203476A1 (en) 2009-07-16
TWI341332B (en) 2011-05-01
KR20090102791A (ko) 2009-09-30
KR101033711B1 (ko) 2011-05-09
CN101680071B (zh) 2012-12-26
JPWO2009087990A1 (ja) 2011-05-26
EP2180076B1 (de) 2016-03-30
TW200940725A (en) 2009-10-01
CN101680071A (zh) 2010-03-24
US20100139820A1 (en) 2010-06-10
JP4590012B2 (ja) 2010-12-01

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