EP2592168B1 - Tôle en acier résistant à l'abrasion avec excellentes propriétés de résistance aux chocs, et procédé de production de ladite tôle en acier - Google Patents

Tôle en acier résistant à l'abrasion avec excellentes propriétés de résistance aux chocs, et procédé de production de ladite tôle en acier Download PDF

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Publication number
EP2592168B1
EP2592168B1 EP11188814.5A EP11188814A EP2592168B1 EP 2592168 B1 EP2592168 B1 EP 2592168B1 EP 11188814 A EP11188814 A EP 11188814A EP 2592168 B1 EP2592168 B1 EP 2592168B1
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EP
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Prior art keywords
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steel plate
abrasion resistant
resistant steel
temperature
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EP11188814.5A
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German (de)
English (en)
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EP2592168A1 (fr
Inventor
William Timms
Ewan Maclean
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British Steel PLC
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Tata Steel UK Ltd
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Classifications

    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0426—Hot rolling
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0463—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/26—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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • 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

Definitions

  • the present invention relates to an abrasion resistant steel plate having excellent impact toughness and also relates to a method for manufacturing such an abrasion resistant steel plate having excellent impact toughness.
  • Tata Steel have been producing and marketing such steels as ABRAZO ® for many years.
  • Increasing of the hardness is effective in improving the abrasion resistance.
  • 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 breaking or cracking and have low impact properties.
  • having a high degree of hardness for a steel plate is disadvantageous for achieving favourable impact properties and workability.
  • the abrasion resistance and impact properties are generally mutually opposing properties.
  • an HB500 class abrasion resistant steel plate (with a Brinell hardness at room temperature of approximately 450 to 550) exhibits excellent abrasion resistance, but has relatively poor impact properties.
  • a steel having a lower degree of hardness such as an HB400 class abrasion 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 favourable workability, but cannot exhibit totally satisfactory impact properties
  • imparting a abrasion resistant steel having an HB400 class room temperature hardness with good impact properties properties could be said to be one effective method of achieving a combination of favourable bending workability and superior abrasion resistance at high temperatures.
  • the japanese published patent application JP11071631 discloses a steel composition that has been designed to provide both high wear resistance together with enhanced toughness for use in such applications as members in construction equipment.
  • An abrasion 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.
  • abrasion resistant steel plate having a hardness value HB value (Brinell hardness) at 25°C of at least 360 HB. It is also an object of the invention to provide a process to provide such an abrasion resistant steel plate.
  • an abrasion resistant steel plate having excellent impact toughness comprising in wt.%
  • the C content is set to not less than 0.10% and not more than 0.35%.
  • Si is a particularly effective element for improving the abrasion resistance, particularly at somewhat elevated temperatures, and is also an inexpensive alloy element.
  • the added amount of Si is set to not less than 0.10% but less than 0.5%.
  • 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 0.8%. Since Mn enhances the hardenability, it is preferable to add Mn in a large amount for the purpose of ensuring more favourable room temperature hardness within the plate thickness center portion of a plate having a thickness of up to 50 mm. In terms of enhancing the impact properties, the upper limit for the Mn content is 1.8%.
  • the P is a harmful element that causes deterioration in the bending workability and the toughness, and is present in the steel 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. However, since 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 abrasion resistance, and is therefore added in an amount of at least 0.1%.
  • excessive addition of Cr can cause a reduction in the toughness, and therefore the Cr content is limited to not more than 1.0%.
  • Mo improves the abrasion resistance, and adding a small amount in the presence of Nb produces a large improvement in the hardenability. For this reason, at least 0.05% 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 0.70%.
  • 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.
  • Ti may be added to fix N as TiN; thereby, the formation of BN 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 abrasion resistance at the higher temperatures of above 300°C. Accordingly, the added amount of Ti is limited to not more than 0.030%.
  • Nb is an optional element in the steel according to the invention. Nb, due to its existence in a solid solution state within the steel plate, can be effective in improving the abrasion 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 dissolve 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 0.08% or lower.
  • 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%.
  • V is an element that is effective in improving the abrasion 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%, preferably to not more than 0.15%. A suitable minimum vanadium content is 0.015%. A suitable maximum content is 0.10% or even 0.08%.
  • the element composition of the present invention is also restricted so that the value of S + P + N + Al + Nb + Ca is not more than 0.09%;
  • 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 abrasion resistant steel plate of the present invention described above.
  • the slab Prior to being hot rolled, the slab may also be subjected to a dehydrogenation treatment, e.g. by allowing the slab to (very) slowly cool under insulated hoods after casting. The cooling process may take days or even weeks.
  • the heating temperature for the slab is 1150°C or higher. However, if a heating temperature is too high, coarsening of the austenite structures occurs and a deterioration in the toughness is the likely result. Therefore, the heating temperature for the slab is preferably not more than 1350°C.
  • the hot rolling is preferably finished at a temperature of not less than 900°C. Furthermore, the hot rolling finishing temperature preferably is not higher than 960°C.
  • slow cooling to ambient temperature or at least below 200°C is conducted.
  • the slow cooling may consist of natural air cooling.
  • the cooling rate may also be reduced to reduce the potentially deleterious effects of hydrogen by allowing the steel to dehydrogenate.
  • this reduced cooling treatment entails a slow cooling from 550 to 350°C, e.g. by stacking a number of plates to cool down simultaneously thereby reducing the cooling rate. In some cases the plate may be reheated to a temperature of about 600°C to achieve the same effect.
  • the desired microstructure By reheating the rolled steel after the slow cooling down to ambient temperatures to a temperature of above the Ac3 transformation point, and then subjecting the plate to accelerated cooling to a temperature of 200°C or lower, the desired microstructure can be produced.
  • 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.
  • the thickness of the plates was 25 mm.
  • the slab thickness was 225 mm.
  • the reheating temperature prior to hot rolling was 1200°C and the finish hot rolling temperature was 950°C.
  • the heat treatment was performed at 930°C for 45 minutes and the cooling rate after the heat treatment was about 20°C/s in the centre of the plate.
  • the microstructure consists of martensite or a mixture of martensite and bainite and the hardness values were measured between 388 and 415 HB (Brinell Hardness).
  • the Charpy Impact values at -40°C were al above 27J ranging.

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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)
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  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)

Claims (14)

  1. Une tôle d'acier résistant à l'abrasion présentant une excellente résistance aux chocs, et comprenant, en % de poids:
    • C: pas moins de 0.10% et pas plus de 0.35;
    • Si: pas moins de 0.10% mais moins de 0.50;
    • Mn: pas moins de 0.8%, pas plus de 1.8, et, de préférence, pas plus de 1.6%;
    • Cr: pas moins de 0.1% et pas plus de 1.0%;
    • Mo: pas moins de 0.05% et pas plus de 0.70%;
    • P: pas plus de 0.020%;
    • S: pas plus de 0.010%;
    • Nb: pas plus de 0.08%;
    • Ti: pas plus de 0.10%:
    • V: pas plus de 0.20%;
    • B: pas moins de 0.0005% et pas plus de 0.0030%;
    • Al: pas moins de 0.01% et pas plus de 0.20%;
    • Ca: pas moins de 0.0005% et pas plus de 0.0030%;
    • N: pas plus de 0.010%;
    • Cu: pas plus de 1.5%;
    • dans lequel S + P + N + Al + Nb + Ca ne dépasse pas 0.09%;
    • dans lequel la valeur de Al:N est 8 ou davantage et/ou la tôle d'acier comprend du Nb dans une proportion supérieure à 0.03%;
    • le restant étant du Fe et des impuretés inévitables
  2. Une tôle d'acier résistant à l'abrasion selon la revendication 1, dans laquelle (Ti/3.42) + (Al/1.92) > N afin d'empêcher la formation de nitrure de bore.
  3. Une tôle d'acier résistant à l'abrasion selon la revendication 1 ou 2, dans laquelle la microstructure est principalement de la bainite, de la martensite, ou de la martensite trempée.
  4. Une tôle d'acier résistant à l'abrasion selon une quelconque des revendications 1 à 3, dans laquelle la microstructure est principalement un mélange de deux ou plusieurs des suivantes: bainite, de martensite, et martensite trempée.
  5. Une tôle d'acier résistant à l'abrasion selon une quelconque des revendications 1 à 4, présentant, à l'essai de Charpy, une résilience minimale à l'impact de 27 J à -40°C lorsqu'on la mesure dans le sens longitudinal.
  6. Une tôle d'acier résistant à l'abrasion selon une quelconque des revendications 1 à 5, dont la valeur HB (dureté Brinell) à 25°C est au minimum 360.
  7. Une tôle d'acier résistant à l'abrasion selon une quelconque des revendications 1 à 6, dont la valeur HB à 25°C est au maximum 440 HB.
  8. Une tôle d'acier résistant à l'abrasion selon une quelconque des revendications 1 à 7, dont la valeur Nb est comprise entre 0.03 et 0.07%.
  9. Un procédé pour la production de la tôle d'acier résistant à l'abrasion comprenant les étapes suivantes:
    a. Production d'une brame d'acier par coulée de lingots, coulée continue de brames épaisses, ou coulée continue de brames minces comprenant, en % de poids:
    • C: pas moins de 0.10% et pas plus de 0.35;
    • Si: pas moins de 0.10% mais pas plus de 0.50;
    • Mn: pas moins de 0.8% et pas plus de 1.8, et, de préférence, pas plus de 1.6%;
    • Cr: pas moins de 0.1% et pas plus de 1.0%;
    • Mo: pas moins de 0.05% et pas plus de 0.70%;
    • P: pas plus de 0.020%;
    • S: pas plus de 0.010%;
    • Nb: pas plus de 0.08%;
    • Ti: pas plus de 0.10%:
    • V: pas plus de 0.20%;
    • B: pas moins de 0.0005% et pas plus de 0.0030%;
    • Al: pas moins de 0.01% et pas plus de 0.20%;
    • Ca: pas moins de 0.0005% et pas plus de 0.0030%;
    • N: pas plus de 0.010%;
    • Cu: pas plus de 1.5%;
    • dans lequel S + P + N + Al + Nb + Ca ne dépasse pas 0.09%;
    • dans lequel la valeur de Al:N est 8 ou davantage et/ou la tôle d'acier comprend du Nb dans une proportion supérieure à 0.03%;
    • le restant étant du Fe et des impuretés inévitables
    b. chauffage de ladite brame à une température d'au moins 1150°C;
    c. laminage à chaud de ladite brame pour former une tôle laminée à chaud, et finissage dudit laminage à chaud à une température non inférieure à 900°C;
    d. refroidissement lent de ladite tôle laminée à chaud résultant du refroidissement naturel à l'air ou plus lentement, jusqu'à 200°C ou une température inférieure;
    e. réchauffement de ladite tôle refroidie à une température supérieure à la température de transformation Ac3
    f. trempe de ladite tôle réchauffée pour former la microstructure désirée, dans laquelle la vitesse de trempe est égale au moins à 5°C/s au centre de la tôle.
  10. Un procédé selon la revendication 9, dans lequel (Ti/3.42) + (Al/1.92) > N afin d'empêcher la formation de nitrure de bore préalablement à la trempe.
  11. Un procédé selon une quelconque des revendications 9 à 10, dans lequel la microstructure désirée est principalement de la bainite, de la martensite, ou de la martensite trempée.
  12. Un procédé selon une quelconque des revendications 9 à 11, dans lequel la microstructure désirée est principalement un mélange de deux ou plusieurs des suivantes: bainite, de martensite, et martensite trempée.
  13. Un procédé selon une quelconque des revendications 9 à 12, dans lequel à l'essai de Charpy, la résilience minimale à l'impact de la tôle est 27 J à -40°C lorsqu'on la mesure dans le sens longitudinal.
  14. Un procédé selon une quelconque des revendications 9 à 13, dans lequel la valeur HB à 25°C est au minimum 360 et/ou au maximum 440 HB.
EP11188814.5A 2011-11-11 2011-11-11 Tôle en acier résistant à l'abrasion avec excellentes propriétés de résistance aux chocs, et procédé de production de ladite tôle en acier Revoked EP2592168B1 (fr)

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EP11188814.5A EP2592168B1 (fr) 2011-11-11 2011-11-11 Tôle en acier résistant à l'abrasion avec excellentes propriétés de résistance aux chocs, et procédé de production de ladite tôle en acier

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JP6235221B2 (ja) * 2013-03-28 2017-11-22 Ｊｆｅスチール株式会社 低温靭性および耐水素脆性を有する耐磨耗厚鋼板およびその製造方法
CN105506504A (zh) * 2014-09-26 2016-04-20 鞍钢股份有限公司 一种超高强度耐磨钢板及其生产方法
KR101899687B1 (ko) 2016-12-22 2018-10-04 주식회사 포스코 고경도 내마모강 및 이의 제조방법
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
US11408048B2 (en) 2017-05-24 2022-08-09 Tata Steel Uk Limited High-strength, hot rolled abrasive wear resistant steel strip
JP7319518B2 (ja) * 2019-02-14 2023-08-02 日本製鉄株式会社 耐摩耗厚鋼板
JP7353393B2 (ja) * 2020-09-10 2023-09-29 Ｊｆｅスチール株式会社 溶接継手及び溶接継手の製造方法
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