• 专利附录
  • 专利说明
  • 权利要求
  • 类似技术
  • 同族专利
  • 引用文献
  • 法律状态
  • 优先权
    • 专利摘要:
    patent summary: "abrasion resistant steel plate which has excellent low temperature toughness and excellent corrosive wear resistance". An abrasion resistant steel plate is provided which has excellent abrasion resistance, excellent low temperature toughness and excellent corrosive wear resistance. An abrasion resistant steel plate includes the composition containing by weight%: 0.23% to 0.35% w, 0.05% to 1.00% wt, 0.1% to 2.0% wt. mn, 0.020% or less of p, 0.005% or less of s, 0.005% to 0.100% of ai, 0.03% to 2.0% of cr and 0.03% to 1.0% of hand in one state wherein di * defined by formula (1) below is satisfied as 45 or more, and additionally containing remaining f and unavoidable impurities as a balance. the steel plate has a structure in which a martensitic phase in the cooled condition forms a main phase and a previous austenite grain grain size is 30 µm or less, and the steel plate surface hardness is 450 or greater in hardness. brinel hbw10 / 3000.
    公开号:BR112015005951B1
    申请号:R112015005951-1
    申请日:2013-09-13
    公开日:2019-09-17
    发明作者:Shinichi Miura；Keiji Ueda；Nobuyuki Ishikawa；Naoki Takayama
    申请人:Jfe Steel Corporation；
    IPC主号:
    专利说明:

    TECHNICAL FIELD [001] The present invention relates to an abrasion resistant steel plate used in an appropriate manner for parts of industrial machines, transport machines and the like. The abrasion-resistant steel plate according to the present invention has excellent low temperature toughness and can be used appropriately as parts that are used in places where wear or abrasion is generated due to contact of the steel plate resistant to abrasion with earth and sand containing water, must be taken into account in particular.
    BACKGROUND TECHNIQUE [002] Conventionally, in relation to parts for industrial machinery, transport machinery and the like such as, for example, an excavator, bulldozer, hopper, bucket or dump truck used at a construction site, a civil engineering yard, a mine or similar, abrasion is generated due to contact of the part with earth, sand or similar. Thus, when manufacturing the parts mentioned above, a steel material that has excellent abrasion resistance is used to extend the life of the parts. In an environment in real use, various states such as a dry state or a wet state are considered to be a land, sand or similar state. In particular, there may be a case where the earth, sand or the like in a wet state contains a corrosive material. In this case, wear due to soil, sand or the like in a wet state becomes wear in an environment that contains the corrosive material, that is, so-called corrosive wear. This des
    Petition 870190051900, of 6/3/2019, p. 4/61
    2/51 corrosive wear is known as an extremely severe wear environment. In view of the above, there is a demand for an abrasion resistant steel material that has excellent resistance to corrosive wear.
    [003] The use of these industrial machines, transport machines and the like in a low temperature zone of 0 ° C or less is also considered. Thus, a steel material that is used for parts of these industrial machines, transport machines and the like is required to have excellent low temperature toughness in addition to abrasion resistance and corrosive wear resistance.
    [004] In order to satisfy such a requirement, for example, Patent Literature 1 proposes a method for manufacturing a high hardness abrasion resistant steel that has excellent low temperature toughness, where hot rolling is applied to a plate of steel that has the composition containing in mass%: 0.30% to 0.50% of C, appropriate amounts of Si, Mn, Al, N, Ti, Nb and B respectively, and 0.10% to 0, 50% Cr and 0.05% to 1.00% Mo, afterwards, the quenching treatment is applied to the hot-rolled plate from a transformation point temperature of Ar3 or above and subsequently to the cooled plate it is hardened thereby obtaining high strength abrasion resistant steel. According to the description of the technique described in Patent Literature 1, the improvement of the hardenability of the steel and the improvement of toughness at low temperature through reinforcement of grain contours are achieved by allowing the steel to contain a large amount of Cr and a large amount of Mo. In addition, according to the description of the technique described in Patent Literature 1, further improvement in low temperature toughness is achieved by applying the tempering treatment to steel.
    [005] Patent Literature 2 proposes a resis steel plate
    Petition 870190051900, of 6/3/2019, p. 5/61
    3/51 try the high tenacity abrasion that the composition contains in mass%: 0.18% to 0.25% C, 0.10% to 0.30% Si, 0.03% to 0, 10% Mn, appropriate amounts of Nb, Al, N and B respectively, 1.00% to 2.00% Cr, and Mo more than 0.50% to 0.80%, and exhibits excellent toughness and excellent strength to delayed fracture after water quenching and tempering. According to the description of a technique described in Patent Literature 2, suppressing the Mn content at a low level, and allowing the steel plate to contain a large amount of Cr and a large amount of Mo, the The hardness of the steel plate can be improved so that the predetermined hardness can be guaranteed and, at the same time, the toughness and resistance to delayed fracture can be improved. In addition, according to the description of the technique described in Patent Literature 2, low temperature toughness is further improved by applying tempering.
    [006] Patent Literature 3 proposes an abrasion resistant and high tenacity steel that has a composition containing in% by mass: 0.30% to 0.45% of C, 0.10% to 0.50% of Si, 0.30% to 1.20% Mn, 0.50% to 1.40% Cr, 0.15% to 0.55% Mo, 0.0005% to 0.0050% B, 0.015% to 0.060% sunshine. Al, and appropriate amounts of Nb and / or Ti. According to the description of the technique described in Patent Literature 3, steel contains a large amount of Cr and a large amount of Mo and, therefore, the hardenability of the steel is improved and, at the same time, grain contours are reinforced, thereby improving low temperature toughness.
    [007] Patent Literature 4 proposes a method for the manufacture of an abrasion resistant steel, in which hot rolling is applied to steel that has a composition containing in mass%: 0.05% to 0.40% of C, 0.1% to 2.0% of Cr, in addition, appropriate amounts of Si, Mn, Ti, B, Al and N respectively and, additionally
    Petition 870190051900, of 6/3/2019, p. 6/61
    4/51 te, Cu, Ni, Mo and V as arbitrary components at a cumulative reduction ratio of 50% or more in a non-recrystallized austenitic temperature range at a temperature of 900 ° C or less, afterwards, the quench is applied to a hot-rolled plate from a transformation point temperature of Ar3 or above and subsequently the cooled plate is quenched, in this way, abrasion resistant steel is obtained. According to the description of this technique, abruptly cooling and directly tempering the elongated austenite grains results in the tempered martensitic structure in which the previous austenite grains are elongated. The tempered martensitic structure of the elongated grains noticeably improves low temperature toughness.
    [008] Additionally, Patent Literature 5 proposes an abrasion resistant steel plate that has excellent low temperature toughness and that has the composition containing in mass%: 0.10% to 0.30% of C, 0, 05% to 1.0% Si, 0.1% to 2.0% Mn, 0.10% to 1.40% W, 0.0003% to 0.0020% B, 0.005% to 0 , 10% Ti and / or 0.035% to 0.1% Al. In the description of the technique described in Patent Literature 5, the abrasion resistant steel plate may additionally contain one or more types of elements selected from a group consisting of Cu, Ni, Cr and V. Due to this composition, it is considered that the abrasion-resistant steel plate has high surface hardness and exhibits excellent abrasion resistance and excellent low temperature toughness.
    [009] Additionally, in Patent Literature 6, an abrasion-resistant steel plate that has excellent curvature property is described. The technique described in Patent Literature 6 refers to an abrasion resistant steel plate that has the composition containing in% by weight: 0.05% to 0.30% of C, 0.1% to 1.2% of Ti, and not more than 0.03% of solute C, and which has the structure in which a matrix
    Petition 870190051900, of 6/3/2019, p. 7/61
    5/51 is formed from a ferrite phase and a hard phase is dispersed in the matrix. The abrasion-resistant steel plate described in Patent Literature 6 may additionally contain one or two types of components selected from a group consisting of Nb and V, one or two types of components selected from a group consisting of Mo and W, one or two types of components selected from a group consisting of Si, Mn and Cu, one or two types of components selected from a group consisting of Ni and B, and Cr. Due to such composition, in relation to the abrasion-resistant steel plate described in Patent Literature 6, it is considered that both the abrasion resistance against abrasion caused by earth and sand and the curvature property can be improved without inducing the increase of notorious hardness.
    CITATION LIST
    PATENT LITERATURE [0010] PTL 1: Document No. JP-A-H08-41535 [0011] PTL 2: Document No. JP-A-H02-179842 [0012] PTL 3: Document No. JP-A-S61- 166954 [0013] PTL 4: Document No. JP-a-2002-20837 [0014] PTL 5: Document No. JP-a-2007-92155 [0015] PTL 6: Document No. JP-a-2007-197813 SUMMARY THE INVENTION PROBLEM OF THE TECHNIQUE [0016] The respective techniques described in Patent Literature 1 to 5 are for the acquisition of steel plates that have low temperature toughness and abrasion resistance. Additionally, the technique described in Patent Literature 6 is for the acquisition of the steel plate which has both curvature property and abrasion resistance. However, in none of these Patent Literatures, wear in an environment that contains a corrosive material such as
    Petition 870190051900, of 6/3/2019, p. 8/61
    6/51 earth and sand in a wet state has been studied and, therefore, there is a disadvantage that consideration is not given sufficiently in relation to corrosive wear resistance.
    [0017] Additionally, in the respective techniques described in Patent Literature 1 to 4, tempering is a requirement and, therefore, there is a disadvantage in which a manufacturing cost is increased. In the technique described in Patent Literature 5, the steel plate contains W as an indispensable component and, therefore, there is a disadvantage in which a manufacturing cost is increased. In the technique described in Patent Literature 6, the main phase is formed of ferrite and, therefore, there is a problem in which the surface hardness is low, therefore, the steel plate cannot acquire sufficient abrasion resistance.
    [0018] The present invention was produced to overcome the disadvantages of the related technique mentioned above, and it is an objective of the present invention to provide an abrasion resistant steel plate that can be manufactured at a low cost, has excellent abrasion resistance and has as much excellent low temperature toughness as well as excellent resistance to corrosive wear.
    SOLUTION TO THE PROBLEM [0019] In order to achieve the objective mentioned above, the inventors of the present invention carried out extensive studies on the influence of various factors exerted on the abrasion resistance, low temperature toughness and corrosive wear resistance of the steel plate. As a result of the studies, the inventors found that the corrosive wear resistance of a steel plate can be noticeably improved by making the steel plate have the composition containing appropriate amounts of Cr and Mo as indispensable components. It is assumed that by allowing the steel plate to contain Cr and Mo, even when the steel plate is exposed to
    Petition 870190051900, of 6/3/2019, p. 9/61
    7/51 earth and sand in a wet state that has pH in a varied range, Cr and Mo exist as an oxyacid and therefore corrosive wear is suppressed.
    [0020] The inventors also found that the abrasion resistance and corrosive wear resistance against abrasion caused by earth and sand can be noticeably improved by keeping the surface hardness of the steel plate at a high level since the steel plate steel has the composition mentioned above.
    [0021] The inventors also found that the excellent toughness at low temperature of the steel plate can certainly be acquired while the excellent abrasion resistance is guaranteed by allowing the steel plate to contain appropriate amounts of Cr and Mo as indispensable components and to contain appropriate amounts of at least C, Si, Mn, P, S, Al, Cr, Mo in a state where DI * defined by the following formula (1) is satisfied 45 or more to improve the hardness of the steel plate, then making the structure in which a martensitic phase in the cooled condition forms a main phase with guaranteed surface hardness of 450 or more in Brinel HBW 10/3000 hardness and additionally making the martensitic phase in the cooled condition finer so that a grain size of grains of previous austenite (γ) is 30 pm or less.
    DI * = 33.85x (0.1xC) 0 ' 5 x (0.7xSi + 1) x (3.33xMn + 1) x (0.35xCu + 1) x (0.36xNi +1) x (2, 16xCr + 1) x (3xMo + 1) x (1.75xV + 1) (1) [0022] (where, C, Si, Mn, Cu, Ni, Cr, Mo and V denote the contents (% by mass) ) of respective elements) [0023] The present invention was carried out on the basis of the findings mentioned above and was completed after further study of the findings. That is, the main point of the invention is as follows.
    [0024] (1) An abrasion-resistant steel plate that has excellent low temperature toughness and excellent resistance to de
    Petition 870190051900, of 6/3/2019, p. 10/61
    8/51 wear corrosive, and the steel plate has the composition containing in% by mass: 0.23% to 0.35% of C, 0.05% to 1.00% of Si, 0.1% to 2.0% Mn, 0.020% or less P, 0.005% or less S, 0.005% to 0.100% Al, 0.03% to 2.0% Cr, and 0.03% to 1.0 % Mo in a state in which DI * defined by the following formula (1) is satisfied 45 or more, and additionally containing remaining Fe and unavoidable impurities as a balance, the steel plate that has a structure in which a martensitic phase in the condition cooled forms a main phase and a grain size of previous austenite grains is 30 pm or less, and the surface hardness of the steel plate is 450 or greater in Brinel HBW10 / 3000 hardness.
    FORMULA
    DI * = 33.85x (0.1xC) 0 ' 5 x (0.7xSi + 1) x (3.33xMn + 1) x (0.35xCu + 1) x (0.36xNi +1) x (2, 16xCr + 1) x (3xMo + 1) x (1.75xV + 1) (1) [0025] (where, C, Si, Mn, Cu, Ni, Cr, Mo and V in formula (1) refer to according to the contents (% by mass) of the respective elements.) [0026] (2) In the abrasion-resistant steel plate described in (1), the steel composition additionally contains, in mass%, one or two or more types of components selected from a group consisting of 0.005% to 0.1% Nb, 0.005% to 0.1% Ti, and 0.005% to 0.1% V.
    [0027] (3) In the abrasion-resistant steel plate described in (1) or (2), the steel composition additionally contains, in mass%, one or two types of components selected from a group consisting of 0.005% to 0.2% of Sn and 0.005% to 0.2% of Sb.
    [0028] (4) In the abrasion-resistant steel plate described in any one of (1) to (3), the steel composition additionally contains, in mass%, one or two or more types of components selected from a group consisting of 0.03% to 1.0% Cu, 0.03% to 2.0% Ni and 0.0003% to 0.0030% B.
    Petition 870190051900, of 6/3/2019, p. 11/61
    9/51 [0029] (5) In the abrasion resistant steel plate described in any one of (1) to (4), the steel composition additionally contains, in mass%, one or two or more types of selected components from a group consisting of 0.0005% to 0.008% REM, 0.0005% to 0.005% Ca and 0.0005% to 0.005% Mg.
    [0030] (6) In the abrasion-resistant steel plate described in any one of (1) to (5), in which the content of the martensitic phase in the cooled condition is 98% or more in terms of volume fraction. ADVANTAGE EFFECTS OF THE INVENTION [0031] According to the present invention, it is possible to manufacture, in an easy and stable way, an abrasion resistant steel plate that has especially excellent resistance to corrosive wear in an environment of earth and sand abrasion in a wet state, which has excellent tenacity at low temperature, and excellent resistance to abrasion in a stable manner without reducing the surface hardness. DESCRIPTION OF THE MODALITIES [0032] First, the reasons for limiting the composition of the abrasion-resistant steel plate of the present invention, which is also called the steel plate in this specification, are explained. In the explanation given below,% by mass is simply expressed by% unless otherwise specified.
    C: 0.23% to 0.35% [0033] C is an element to increase the hardness of the steel plate and to improve the abrasive resistance. When the C content is less than 0.23%, the steel plate does not acquire sufficient hardness. On the other hand, when the C content exceeds 0.35%, weldability, low temperature toughness and workability of the steel plate are reduced. Thus, the C content is limited to a value that is within the range of 0.23% to 0.35%. The C content is preferably limited to a value that is within the range of 0.25% to 0.30%.
    Petition 870190051900, of 6/3/2019, p. 12/61
    10/51
    Si: 0.05% to 1.00% [0034] Si is an effective element that acts as a deoxidizing agent for molten steel. Si is also an element that contributes to the strength improvement of the steel plate by increasing the reinforcement of solid solution. The Si content is set at 0.05% or more to guarantee such effects. When the Si content is less than 0.05%, a deoxidizing effect cannot be achieved sufficiently. On the other hand, when the Si content exceeds 1.00%, the ductility and toughness of the steel plate are reduced, and the inclusions content in the steel plate is increased. Thus, the Si content is limited to a value that is within the range of 0.05% to 1.00%. The Si content is preferably limited to a value that is within the range of 0.15% to 0.45%.
    Mn: 0.1% to 2.0% [0035] Mn is an element that has an action to improve the hardenability. To ensure such an effect, the Mn content is set at 0.1% or more. On the other hand, when the Mn content exceeds 2.0%, weakening of the temper occurs and the zone affected by heat from welding becomes hardened, the weldability is reduced. Thus, the Mn content is limited to a value that is within the range of 0.1% to 2.0%. The Mn content is preferably limited to a value that is within the range of 0.4% to 1.7%. It is more preferable that the Mn content is limited to a value that is within the range of 0.5% to 1.0%.
    P: 0.020% or less [0036] When the P content in steel is large, the reduction of toughness at the low temperature of the steel plate is induced and, therefore, it is desirable that the P content is as low as possible. In the present invention, the permissible P content is 0.020%. The excessive reduction of the P content induces a sharp increase in a refining cost. Thus, it is desirable to establish the P content at 0.005% or more.
    [0037] S: 0.005% or less
    Petition 870190051900, of 6/3/2019, p. 13/61
    11/51 [0038] When the S content in steel is large, S is precipitated as MnS. In high-strength steel, MnS becomes a starting point for the occurrence of fracture and induces deterioration in the toughness of the steel plate and, therefore, it is desirable that the S content be as low as possible. In the present invention, the permissible S content is 0.005%. Thus, the S content is limited to 0.005% or less. Excessive reduction in the S content induces a sharp increase in refining costs. Thus, it is desirable to set the S content to 0.0005% or more.
    Al: 0.005% to 0.100% [0039] Al is an element that acts as a deoxidizing agent for molten steel. Additionally, Al contributes to the improvement of toughness at low temperature due to the refining of crystal grains. In order to achieve such an effect, the Al content is set at 0.005% or more. When the Al content is less than 0.005%, such an effect cannot be sufficiently acquired. On the other hand, when the Al content exceeds 0.100%, the weldability of the steel plate is reduced. Thus, the Al content is limited to a value that is within the range of 0.005% to 0.100%. The Al content is preferably limited to a value that is within the range of 0.015% to 0.050%.
    Cr: 0.03% to 2.0% [0040] Cr has an effect of increasing the hardenability. Cr also has an effect of improving toughness at low temperature due to the refining of a martensitic phase. Thus, in the present invention, Cr is an important element. Additionally, in a corrosive wear environment in which a contact between a steel plate and earth and sand or the like in a wet state becomes a problem, Cr is dissolved as a chromate ion due to an anodic reaction, and suppresses corrosion due to an inhibitory effect thus giving rise to an effect of improving the corrosion resistance of the steel plate. To achieve such an effect, the Cr content is set at 0.03% or
    Petition 870190051900, of 6/3/2019, p. 14/61
    12/51 more. When the Cr content is less than 0.03%, the steel plate cannot exhibit such an effect sufficiently. On the other hand, when the Cr content exceeds 2.0%, weldability is reduced and a manufacturing cost is sharply increased. Thus, the Cr content is limited to a value that is within the range of 0.03% to 2.0%. The Cr content is preferably limited to a value that is within the range of 0.07% to 1.0%. It is more preferable that the Cr content is limited to a value that is within the range of 0.2% to 0.9%.
    Mo: 0.03% to 1.0% [0041] Mo has an effect of increasing the hardenability. Mo also has an effect of improving low temperature toughness due to refining a martensitic phase. Thus, in the present invention, Mo is an important element. Additionally, in a corrosive wear environment in which a contact between a steel plate and earth and sand or the like in a wet state becomes a problem, Mo is dissolved as a molybdate ion due to an anodic reaction, and suppresses corrosion through a inhibitory effect, thus giving rise to an effect of improving resistance to corrosive wear. In order to achieve this effect, the Mo content is set at 0.03% or more. When the Mo content is less than 0.03%, the steel plate cannot exhibit such an effect sufficiently. On the other hand, when the Mo content exceeds 1.0%, the weldability of the steel plate is reduced and the manufacturing cost is sharply increased. Thus, the Mo content is limited to a value that is within the range of 0.03% to 1.0%. The Mo content is preferably limited to a value that is within the range of 0.10% to 0.50%. It is more preferable that the Mo content is limited to a value that is within the range of 0.20% to 0.40%.
    [0042] Containing Cr and Mo in a combined way on the steel plate, it is expected that the resistance to corrosive wear can be noticeably improved. It is based on the estimate that Cr and
    Petition 870190051900, of 6/3/2019, p. 15/61
    13/51
    Mo have different pH regions in which Cr or Mo can exist as an oxygen acid and therefore corrosive wear caused by earth and sand or the like in a wet state that has a pH over a wide range can be suppressed.
    [0043] The components mentioned above are the basic components of steel. The abrasion-resistant steel plate according to the present invention can additionally contain, in addition to the basic components mentioned above, as an optional element or optional elements, one or two or more types of components selected from a group consisting of 0.005% to 0.1% Nb, 0.005% to 0.1% Ti, and 0.005% to 0.1% V and / or one or two types of components selected from a group that consists of 0.005% to 0.2% of Sn and 0.005% to 0.2% of Sb and / or one or two or more types of components selected from a group consisting of 0.03% to 1.0% Cu, 0.03% to 2.0% Ni, and 0.0003% to 0.0030% B and / or one or two or more types of components selected from a group consisting of 0.0005 % to 0.008% REM, 0.0005% to 0.005% Ca and 0.0005% to 0.005% Mg.
    [0044] One or two or more types of components selected from a group consisting of 0.005% to 0.1% Nb, 0.005% to 0.1% Ti and 0.005% to 0.1% V.
    [0045] All of Nb, Ti and V are elements that precipitate as precipitates, and improve the toughness of steel through refining the structure. The abrasion-resistant steel plate according to the present invention, when necessary, contains one or two or more types of components selected from a group consisting of Nb, Ti and V.
    [0046] Nb is an element that precipitates as a carbonitride and contributes to the improvement of toughness through refining the structure. The Nb content can be set at 0.005% or more for
    Petition 870190051900, of 6/3/2019, p. 16/61
    14/51 obtain such an effect. On the other hand, when the Nb content exceeds 0.1%, weldability can be reduced. When steel contains Nb, the Nb content is preferably limited to a value that is within the range of 0.005% to 0.1%. The Nb content is most preferably set at a value that is within the range of 0.012% to 0.03% from a refining point of view of the structure.
    [0047] Ti is an element that precipitates as TiN and contributes to the improvement of toughness through fixation of solid solute N. The Ti content is established at 0.005% or more to achieve such an effect. On the other hand, when the Ti content exceeds 0.1%, coarse carbonitride precipitates so that the toughness is reduced in some cases. When the steel contains Ti, the Ti content is preferably limited to a value that is within the range of 0.005% to 0.1%. The Ti content is preferably limited to a value that is within the range of 0.005% to 0.03% from the point of view of reducing a manufacturing cost.
    [0048] V is an element that precipitates as a carbonitride and contributes to the improvement of toughness through a refining effect of the structure. The V content is set at 0.005% or more to achieve such an effect. On the other hand, when the V content exceeds 0.1%, weldability is reduced in some cases. Thus, when steel contains V, the V content is preferably limited to a value that is within the range of 0.005% to 0.1%.
    [0049] One or two types of components selected from a group consisting of 0.005% to 0.2% Sn and 0.005% to 0.2% Sb [0050] Both Sn and Sb are elements that improve wear resistance corrosive. The abrasion-resistant steel plate according to the present invention, when necessary, contains one or two types of elements selected from a group consisting of Sn and Sb.
    Petition 870190051900, of 6/3/2019, p. 17/61
    15/51 [0051] Sn is dissolved as Sn ion due to an anodic reaction, and suppresses corrosion through an inhibitory effect, thereby improving the corrosive wear resistance of a steel plate. In addition, Sn forms an oxide film containing Sn on a surface of the steel plate and therefore an anodic reaction and a cathodic reaction of the steel plate are suppressed, thereby improving the corrosive wear resistance of the steel plate. The Sn content is set at 0.005% or more to achieve such an effect. On the other hand, when the Sn content exceeds 0.2%, deterioration in the ductility and toughness of the steel plate can be induced. Thus, when the steel contains Sn, the Sn content is preferably limited to a value that is within the range of 0.005% to 0.2%. The Sn content is most preferably set at a value that is within the range of 0.005% to 0.1% from the point of view of reducing residual elements.
    [0052] Sb suppresses corrosion of a steel plate by suppressing an anodic reaction of the steel plate and also suppressing a hydrogen generation reaction which is a cathode reaction thereby improving the corrosion resistance of the steel plate. The Sb content is set at 0.005% or more to sufficiently acquire such an effect. On the other hand, when the Sb content exceeds 0.2%, the deterioration of toughness of the steel plate can be induced. Thus, when steel contains Sb, the Sb content is preferably set at a value that is within the range of 0.005% to 0.2%. It is more preferred that the Sb content is set at a value that is within the range of 0.005% to 0.1%.
    [0053] One or two or more types of components selected from a group consisting of 0.03% to 1.0% Cu, 0.03% to 2.0% Ni, and 0.0003% to 0.0030% B.
    [0054] All of Cu, Ni and B are elements that enhance the
    Petition 870190051900, of 6/3/2019, p. 18/61
    16/51 hardenability. The abrasion-resistant steel plate according to the present invention, when necessary, can contain one or two or more types of elements selected from a group consisting of Cu, Ni and B.
    [0055] Cu is an element that contributes to the improvement of temperability. The Cu content can be 0.03% or more to achieve such an effect. On the other hand, when the Cu content exceeds 1.0%, hot workability is reduced, and a manufacturing cost also rises sharply. Thus, when steel contains Cu, the Cu content is preferably limited to a value that is within the range of 0.03% to 1.0%. The Cu content is most preferably limited to a value that is within the range of 0.03% to 0.5% from the point of view of further reducing a manufacturing cost.
    [0056] Ni is an element that also contributes to the improvement of hardenability and the improvement of toughness at low temperature of the steel plate. The Ni content can be 0.03% or more to achieve such an effect. On the other hand, when the Ni content exceeds 2.0%, a manufacturing cost may increase. When steel contains Ni, the Ni content is preferably limited to a value that is within the range of 0.03% to 2.0%. The Ni content is most preferably limited to a value that is within the range of 0.03% to 0.5% from the point of view of further reducing a manufacturing cost.
    [0057] B is an element that contributes to the improvement of temperability with a small amount of steel. The B content can be 0.0003% or more to achieve such an effect. On the other hand, when the B content exceeds 0.0030%, the toughness of the steel plate can be reduced. Thus, when steel contains B, the B content is preferably limited to a value that is within the range of 0.0003% to 0.0030%. The B content is most preferably within
    Petition 870190051900, of 6/3/2019, p. 19/61
    17/51 from a range of 0.0003% to 0.0015% from a cold crack suppression point of view on a welded part formed by low heat input welding such as CO2 welding or similar used in general welding of an abrasion resistant steel plate.
    [0058] One or two or more types of components selected from a group consisting of 0.0005% to 0.008% REM, 0.0005% to 0.005% Ca, and 0.0005% to 0.005% Mg .
    [0059] All of REM, Ca and Mg are elements that form sulfide inclusions combining with S and, therefore, these elements are elements that suppress the formation of MnS. The abrasion-resistant steel plate according to the present invention, when necessary, contains one or two or more types of components selected from a group consisting of REM, Ca and Mg.
    [0060] REM fixes S, thereby suppressing the formation of MnS which causes a reduction in the toughness of the steel plate. The REM content can be 0.0005% or more to achieve such an effect. On the other hand, when the REM content exceeds 0.008%, the inclusions in the steel plate are increased so that the toughness is reduced in some cases. When steel contains REM, the REM content is preferably limited to a value that is within the range of 0.0005% to 0.008%. The REM content is most preferably set at a value that is within the range of 0.0005% to 0.0020%.
    [0061] Ca fixed S thus suppressing the formation of MnS which causes the reduction of toughness. The Ca content can be 0.0005% or more to achieve such an effect. On the other hand, when the Ca content exceeds 0.005%, the inclusions content in the steel is increased and the toughness can be reduced in reverse. When steel contains Ca, the Ca content is preferably limited to a value that is within the range of 0.0005% to 0.005%. The Ca content is more preferably established
    Petition 870190051900, of 6/3/2019, p. 20/61
    18/51 set to a value that is within the range of 0.0005% to 0.0030%.
    [0062] Mg fixes S thereby suppressing the formation of MnS which causes a reduction in the toughness of the steel plate. The Mg content can be preferably 0.0005% or more to achieve such an effect. On the other hand, when the Mg content exceeds 0.005%, the inclusions content in the steel plate is increased and the toughness can be reduced in reverse. When steel contains Mg, the Mg content is preferably limited to a value that is within the range of 0.0005% to 0.005%. It is more preferable that the Mg content is set at a value that is within the range of 0.0005% to 0.0040%.
    [0063] The abrasion-resistant steel plate according to the present invention has the components mentioned above within the ranges mentioned above and in a state in which DI * is satisfied 45 or more. DI * is defined by the following formula (1). In the calculation for DI *, in relation to the elements described in formula (1), the elements not contained in the steel are calculated as Zero.
    DI * = 33.85x (0.1xC) 0 ' 5 x (0.7xSi + 1) x (3.33xMn + 1) x (0.35xCu + 1) x (0.36xNi +1) x (2, 16xCr + 1) x (3xMo + 1) x (1.75xV + 1) (1) [0064] (where, C, Si, Mn, Cu, Ni, Cr, Mo and V are the levels (% by mass) ) of respective elements.) [0065] When DI * is set to less than 45, a quenching depth from a steel plate surface becomes less than 10 mm and therefore a steel plate life as the abrasion-resistant steel plate is reduced. Thus, DI * is limited to 45 or more. The DI * range is preferably set at 75 or more.
    [0066] Remaining, in addition to the compositions mentioned above, are Fe and unavoidable impurities as a balance.
    [0067] Below, the structure and property of the resistant steel plate 870190051900, dated 06/03/2019, p. 21/61
    19/51 to the abrasion of the present invention are explained.
    [0068] The abrasion-resistant steel plate according to the present invention has the composition mentioned above and the structure in which a martensitic phase in the cooled condition forms a main phase and a grain size of austenite grains (γ) previous is 30 pm or less. In addition, the abrasion-resistant steel plate according to the present invention has a surface hardness of 450 or greater in Brinel HBW 10/3000 hardness. In this document, a phase that occupies 90% or more in an area ratio is defined as the main phase.
    [0069] Martensitic phase in the cooled condition: 90% or more in area ratio [0070] When the phase fraction of the martensitic phase in the cooled condition is less than 90% in an area ratio, the steel plate cannot guarantee hardness desired. Thus, when the area ratio is less than 90%, the wear resistance of the steel plate is reduced so that the desired wear resistance cannot be guaranteed. In addition, the steel plate cannot guarantee sufficient low temperature toughness. Additionally, in the tempered martensite phase, Cr and Mo form carbide together with Fe when cementite is formed in the temper. Due to carbide formation, the Cr sol and the Mo solute, which are effective in ensuring corrosion resistance, are reduced. Thus, the martensitic phase is maintained in the martensitic phase in the cooled condition where the martensitic phase is not tempered. A phase fraction of the martensitic phase in the cooled condition is preferably set to 95% or more in the area ratio, and it is more preferable that the phase fraction of the martensitic phase in the cooled condition is set to 98% or more in the area ratio.
    [0071] Grain size of previous austenite (γ) grains: 30
    Petition 870190051900, of 6/3/2019, p. 22/61
    20/51 pm or less [0072] Even when the phase fraction of the martensitic phase in the cooled condition can guarantee an area ratio of 90% or more, when a grain size of previous austenite (γ) grains becomes coarse exceeding 30 pm, the low temperature toughness of the steel plate is reduced. As the grain size of previous austenite grains (γ), values that are obtained according to JIS G 0551 after microscopic observation of the structure attacked by a picric acid using an optical microscope (magnification: 400 times) are used .
    [0073] The abrasion-resistant steel plate according to the present invention, which has the composition mentioned above and the structure has a surface hardness of 450 or greater in Brinel HBW hardness 10/3000.
    [0074] Surface hardness: 450 or greater in Brinel HBW 10/3000 hardness [0075] When the surface hardness of steel is less than 450 in Brinel HBW 10/3000 hardness, the service life of the abrasion-resistant steel plate it becomes short. Thus, the surface hardness is set at 450 or greater in Brinel HBW 10/3000 hardness. Brinel hardness is measured according to the stipulation described in JIS Z 2243.
    [0076] In the following, the preferred method of manufacturing the abrasion resistant steel plate of the present invention is explained.
    [0077] The steel material that has the aforementioned composition is produced by casting and then is subjected to hot rolling without cooling when the steel material maintains a predetermined temperature or is subjected to hot rolling after cooling and reheating, thereby making a steel plate that has a desired size and shape.
    [0078] The method of manufacturing the steel material is not particu
    Petition 870190051900, of 6/3/2019, p. 23/61
    21/51 widely limited. It is desirable for molten steel, which has the composition mentioned above, to be produced using a known refining method such as the use of a converter, and a steel material, such as a plate that has a predetermined size, is manufactured using a known casting method such as a continuous casting method. It goes without saying that a steel material can be manufactured using an ingot grinding method.
    [0079] Reheat temperature: 950 to 1,250 ° C [0080] When the reheat temperature is less than 950 ° C, the resistance to deformation becomes excessively high so that a rolling load becomes excessively large, thereby hot lamination may not be performed. On the other hand, when the reheat temperature becomes high exceeding 1,250 ° C, the crystal grains become excessively coarse so that the steel cannot guarantee the desired high toughness. Thus, the reheat temperature is preferably limited to a value that is within the range of 950 to 1,250 ° C.
    [0081] The reheated steel material or steel material that maintains a predetermined temperature without being reheated is then subjected to hot rolling so that a steel plate that has a desired size and a desired shape is manufactured. The condition of hot rolling is not particularly limited. After the hot rolling is completed, it is preferable that the direct tempering treatment in which the steel plate is immediately cooled is applied to the steel plate. It is preferred that a tempering start temperature is set at a temperature not below a transformation point of Ar3. In order to establish the tempering start temperature at the Ar3 transformation point or higher, it is preferable that the hot rolling end temperature
    Petition 870190051900, of 6/3/2019, p. 24/61
    22/51 is set at 800 ° C or more not below the Ar3 transformation point. When the hot rolling finish temperature is excessively high, there may be a case where the crystal grains become coarse. Thus, it is preferred that the hot rolling finish temperature is set at 950 ° C or less. A quench cooling rate is not particularly limited as long as the quench cooling rate is equal to or greater than a cooling rate at which a martensitic phase is formed. It is desirable that the quench cooling rate is as high as possible to prevent a martensitic phase from being self-tempering. The Cr sol and the Mo solute, which are effective for corrosion resistance, form carbide together with Fe when cementite is formed in the self-caking, so that the amount of Cr sol and Mo solute is reduced. Self-warning also reduces a volume fraction of martensite. It is desirable that the quench cooling rate is set at 65 to 75 ° C / s when a plate thickness is 5 to 15 mm, the quench cooling rate is set at 40 to 55 ° C / s when the thickness of plate is 16 to 22 mm, the quench cooling rate is set at 30 to 40 ° C / s when the plate thickness is 22 to 28 mm, and the quench cooling rate is set to 20 to 30 ° C / s s when the plate thickness is 29 to 35 mm. In addition, it is preferred that the cooling interruption temperature is set at 300 ° C or less. It is more preferable that the cooling interruption temperature is 200 ° C or less. In this specification, cooling rate is a cooling rate obtained by calculating a temperature in a central portion of a steel plate by calculating heat transfer heat conduction.
    [0082] After the hot rolling is completed, in place of the direct temper treatment where a steel plate is immediately
    Petition 870190051900, of 6/3/2019, p. 25/61
    23/51 cooled, the treatment can be carried out in which the steel plate is gradually cooled by air after the hot rolling is completed (air cooling) and, subsequently, the steel plate is reheated to a predetermined heating temperature and then the steel plate is cooled. It is desirable that the reheat temperature is set at a value that is within the range of 850 to 950 ° C. A quench cooling rate after reheating is not particularly limited as long as the quench cooling rate after reheating is equal to or greater than a cooling rate at which a martensitic phase is formed. It is desirable that the quench cooling rate is as high as possible to prevent a martensitic phase from being self-tempering. The Cr sol and the Mo solute, which are effective for corrosion resistance, form carbide together with Fe when cementite is formed in the self-caking, so that the amount of Cr sol and Mo solute is reduced. Self-warning also reduces a volume fraction of martensite. It is desirable that the quench cooling rate is set at 65 to 75 ° C / s when a plate thickness is 5 to 15 mm, the quench cooling rate is set at 40 to 55 ° C / s when the thickness of plate is 16 to 22 mm, the quench cooling rate is set at 30 to 40 ° C / s when the plate thickness is 22 to 28 mm, and the quench cooling rate is set to 20 to 30 ° C / s s when the plate thickness is 29 to 35 mm. Additionally, in order to prevent a martensitic phase from being self-tempering, it is preferable that the cooling interruption temperature is set at 300 ° C or less. It is more preferable that the cooling interruption temperature is set at 200 ° C or less.
    [0083] In order to acquire the martensite structure in the cooled condition, the tempering treatment is not carried out after carrying out the treatment mentioned above.
    Petition 870190051900, of 6/3/2019, p. 26/61
    24/51 [0084] Hereinafter, the present invention is further explained on the basis of examples.
    EXAMPLE [0085] The molten steel that has the composition described in Table 1 was produced by a vacuum melting furnace, and was cast in a mold so that ingots (steel material) that have a weight of 150 kgf respectively were manufactured . These steel materials were reheated to the heating temperatures described in Tables 2 (Table 2-1, Table 2-2 and Table 2-3) and, subsequently, the steel materials were subjected to hot rolling under conditions described in Table 2 So, in relation to some steel plates, the direct quenching (DQ) treatment in which the quenching (direct quenching) is carried out immediately after the hot rolling is completed was carried out under the conditions described in Tables 2. steel plates, the reheat quenching (RQ) treatment was carried out in which a steel plate is cooled by air after the hot rolling is completed under the respective conditions described in Tables 2 and the steel plate is reheated to a temperature described in Tables 2 and, later, it is cooled. In the examples described in Table 2-3, cooling rates from 800 ° C to 500 ° C at DQ or RQ were also indicated. In general, for a common C-Mn steel, the transformation during cooling starts at a temperature of approximately 800 ° C and is completed at a temperature of about 500 ° C. Therefore, a cooling rate of 800 ° C to 500 ° C greatly influences the behavior of steel transformation. Thus, the cooling rate of 800 ° C to 500 ° C has generally been used as a representative cooling rate to estimate steel transformation behavior.
    [0086] The specimens were sampled from the manufactured steel plates, and the specimens were subjected to an observation of
    Petition 870190051900, of 6/3/2019, p. 27/61
    25/51 structure, a surface hardness test, a Charpy impact test and a corrosive wear resistance test. The following test methods have been adopted. The results of the observation of the structure, the surface hardness test, the Charpy impact test and the corrosive wear resistance test are shown in Table 3 (Table 3-1, Table 3-2 and Table 3-3).
    (1) STRUCTURE OBSERVATION [0087] The specimens for the observation of structure were sampled from steel plates manufactured in a 1/2 thickness position of the steel plate plate so that an observation surface becomes a cross section parallel to the rolling direction. The observation surface of the specimens for observation of structure was polished and was attacked by a picric acid, thus exposing previous γ grains. Therefore, the observation surfaces were observed with an optical microscope (magnification: 400 times). The equivalent circle diameters of the respective 100 previous γ grain views were measured, an arithmetic mean was calculated based on obtained equivalent circle diameters, and the arithmetic mean was established as the previous γ grain size of the steel plate.
    [0088] Thin-film specimens (specimens for observation of the structure through a transmission electron microscope) were sampled from steel plates manufactured at a position of 1/4 plate thickness of the steel plate in the same way. Then, the thin film specimen was ground and polished (mechanical polishing, electrolytic polishing), thereby forming a thin film. Then, each 20 fields of view of the thin film were observed by a transmission electron microscope (magnification: 20,000 times), a region in which cementite does not precipitate was recognized as a region of martensitic phase, and the area of the region was measured. The area of the region
    Petition 870190051900, of 6/3/2019, p. 28/61
    26/51 The martensitic phase was indicated by a ratio (%) in relation to the total structure, and this ratio was established as a martensitic fraction (area ratio). In addition, a type of phase in which cementite precipitates has been determined.
    (2) SURFACE HARDNESS TEST [0089] The specimens for measuring surface hardness were sampled from manufactured steel plates, and HBW 10/3000 surface hardness was measured according to JIS Z 2243 (1998) . In the hardness measurement, a hard tungsten sphere that has a diameter of 10 mm was used, and a weight was set at 3000 kgf.
    (3) CHARPY IMPACT TEST [0090] V-notched specimens were sampled from steel plates manufactured in a 1/4 thick steel plate position, in the direction (direction C) perpendicular to the direction of lamination, and a Charpy impact test was performed according to the stipulation of JIS Z 2242 (1998). The absorbed energy vE-40 (J) was obtained under the condition of a test temperature at -40 ° C. The number of specimens was three for each of the steel plates, and an arithmetic average of the values obtained from three specimens is respectively established as the absorbed energy vE-40 of the steel plate. The steel plate that has the absorbed energy vE-40 of 30 J or greater was evaluated as the steel plate that has excellent toughness.
    (4) CORROSIVE WEAR RESISTANCE TEST [0091] The wear specimens (size: 10 mm thick, 25 mm wide and 75 mm long) were sampled from steel plates manufactured at a position 1 mm distant from a surface of the manufactured steel plate. These wear specimens were mounted on a wear tester, and a wear test was performed.
    [0092] The wear specimen was mounted on the design tester
    Petition 870190051900, of 6/3/2019, p. 29/61
    27/51 spend so that the wear specimen was perpendicular to a geometric axis of rotation of a tester's rotor and a surface of 25 mm x 75 mm was parallel to the circumferential tangential direction of a rotation circle, the specimen and the rotor were covered with an outer vessel, and a wear material was introduced into the outer vessel. As the wear material, a mixture is used in which silica sand having an average grain size of 0.65 mm and an aqueous NaCl solution that has been prepared so that the concentration becomes 15,000 ppm mass has been mixed together so that a weight ratio between silica sand and the aqueous NaCl solution becomes 3: 2.
    [0093] The test conditions were established so that the rotor was spun at 600 rpm and the outer vessel was spun at 45 rpm. The test was completed on rotor revolutions that became 10,800 times in total. After the test was completed, the weights of the respective specimens were measured. The difference between the weight after the test and the initial weight (= a weight reduction amount) was calculated, and a wear resistance ratio (= (reference value) / (specimen weight reduction amount)) was calculated using a weight reduction amount of the SS400 steel plate stipulated in rolled steel for general structure, tensile strength of the 400 MPa class (JIS G3101) (conventional example) as a reference value. When the wear resistance ratio was 1.5 or more, the steel plate was evaluated as the steel plate that has excellent resistance to corrosive wear.
    Petition 870190051900, of 6/3/2019, p. 30/61
    TABLE 1
    Steel Number Chemical Composition (% by mass) DI * Ar3 (° C) Comments Ç Si Mn P s sol.Al Cr Mo Nb, Ti, V Sn, Sb Cu, Ni, B Ca, REM, Mg THE 0.26 0.33 1.64 0.007 0.0017 0.032 0.05 0.05 - - - - 55.3 693 within the scope of the present invention B 0.23 0.25 1.22 0.008 0.0024 0.027 0.20 0.10 - - - - 56.8 730 within the scope of the present invention Ç 0.24 0.41 0.62 0.007 0.0019 0.025 1.10 0.10 - - Cu: 0.1,Ni: 0.12, B: 0.0021 - 98.0 753 within the scope of the present invention D 0.27 0.25 0.75 0.007 0.0015 0.025 0.38 0.16 Nb: 0.022,Ti: 0.014 - B: 0.0009 - 61.6 748 within the scope of the present invention AND 0.26 0.26 0.65 0.008 0.0013 0.022 0.45 0.11 Nb: 0.025,Ti: 0.017 - B: 0.0013 - 53.5 762 within the scope of the present invention F 0.28 0.30 0.85 0.008 0.0015 0.027 0.25 0.25 Nb: 0.017,Ti: 0.010 - B: 0.0006 - 70.8 731 within the scope of the present invention G 0.26 0.27 0.76 0.008 0.0015 0.027 0.40 0.15 Nb: 0.015,Ti: 0.015 - B: 0.0020 Ca: 0.0022 61.9 751 Within the scope of the present invention H 0.29 0.32 1.23 0.008 0.0018 0.023 0.10 0.06 Ti: 0.022 - - REM: 0.0015 51.6 715 Within the scope of the present invention I 0.27 0.32 1.34 0.008 0.0018 0.023 0.15 0.15 Nb: 0.013,Ti: 0.015 - - - 71.4 705 Within the scope of the present invention J 0.30 0.35 0.50 0.006 0.0022 0.024 0.30 0.65 V: 0.035 - - Ca: 0.0021 100.4 721 Within the scope of the present invention K 0.24 0.32 1.05 0.007 0.0027 0.021 0.12 0.32 Ti: 0.013 - B: 0.0009 Mg: 0.0016 71.2 724 within the scope of the present invention
    28/51
    Petition 870190051900, of 6/3/2019, p. 31/61
    TABLE 1 (CONTINUED)
    Steel Number Chemical Composition (% by mass) DI * Ar3 (° C) Comments Ç Si Mn P s sol.Al Cr Mo Nb, Ti, V Sn, Sb Cu, Ni, B Ca, REM, Mg L 0.31 0.27 0.57 0.007 0.0015 0.023 0.76 0.11 Nb: 0.019, V: 0.016 - B:0.0025 - 74.2 748 Within the scope of the present invention M 0.28 0.30 1.21 0.008 0.0016 0.025 0.13 0.16 Nb: 0.021,Ti: 0.015 - B:0.0013 - 65.3 712 Within the scope of the present invention N 0.26 0.29 1.02 0.007 0.0014 0.019 0.53 0.25 Nb: 0.029,Ti: 0.021, V: 0.034 Sb: 0.066 Ass:0.24, Ni: 0.31 Here:0.0012 138.3 698 Within the scope of the present invention O 0.26 0.36 1.52 0.008 0.0016 0.024 0.02 - Ti: 0.016 - - Here:0.0018 43.2 708 outside the scope of the present invention P 0.29 0.35 1.42 0.007 0.0019 0.025 - 0.02 V: 0.021 - - Mg:0.0032 45.2 705 outside the scope of the present invention Q 0.30 0.38 1.36 0.006 0.0021 0.029 0.01 0.02 - - Ass:0.08 - 45.7 705 outside the scope of the present invention R 0.18 0.24 0.88 0.008 0.0016 0.024 0.28 0.15 Nb: 0.015 Sn: 0.015 B:0.0022 - 48.5 768 outside the scope of the present invention s 0.25 0.31 0.76 0.007 0.0017 0.021 0.09 0.10 Nb: 0.013 Sb: 0.033 Ass:0.1, Ni: 0.09 REM:0.0012 38.2 755 outside the scope of the present invention T 0.28 0.26 1.09 0.007 0.0025 0.024 0.05 0.27 - - - - 62.2 714 within the scope of the present invention U 0.27 0.30 0.93 0.007 0.0019 0.028 0.43 0.19 - - - - 83.5 730 within the scope of the present invention
    29/51
    Petition 870190051900, of 6/3/2019, p. 32/61
    Steel Number Chemical Composition (% by mass) DI * Ar3 ( O C) Comments Ç Si Mn P s sol.Al Cr Mo Nb, Ti, V Sn, Sb Cu, Ni, B Ca, REM, Mg V 0.28 0.25 1.13 0.009 0.0029 0.022 0.52 0.13 - Sn: 0.021 - - 93.6 715 within the scope of the present invention W 0.29 0.36 0.85 0.008 0.0021 0.031 0.75 0.11 Nb: 0.014 Sn: 0.067 - - 96.3 732 within the scope of the present invention
    30/51
    Petition 870190051900, of 6/3/2019, p. 33/61
    TABLE 2-1
    Steel Plate Number Steel Number Plate Thickness (mm) Treatment Type * Hot rolling DQ RQ Reheat Temperature(° C) Lamination termination temperature (° C) Cooling Start Temperature (° C) Cooling After Lamination Cooling Interruption Temperature(° C) Heating Temperature (° C) Cooling Method Cooling Interruption Temperature (° C) 1 THE 12 RQ 1,120 900 - air-cooled - 900 water-cooled 150 2 THE 19 RQ 1,120 920 - air-cooled - 910 water-cooled 170 3 THE 25 DQ 1,120 880 830 water-cooled 150 - - - 4 THE 25 DQ 1,250 950 870 water-cooled 310 - - - 5 THE 25 DQ 1,120 980 900 water-cooled 310 - - - 6 B 12 RQ 1,120 890 - air-cooled - 900 water-cooled 150 7 B 19 DQ 1,120 870 850 water-cooled 150 - - - 8 B 32 DQ 1,120 890 840 water-cooled 150 - - -
    31/51
    Petition 870190051900, of 6/3/2019, p. 34/61
    Steel Plate Number Steel Number Plate Thickness (mm) Treatment Type * Hot rolling DQ RQ Reheat Temperature(° C) Lamination termination temperature (° C) Cooling Start Temperature (° C) Cooling After Lamination Cooling Interruption Temperature(° C) Heating Temperature (° C) Cooling Method Cooling Interruption Temperature (° C) 9 B 32 DQ 1,200 970 900 water-cooled 250 - - - 10 B 32 DQ 1,230 960 900 water-cooled 250 - - - 11 Ç 19 DQ 1,050 840 810 water-cooled 150 - - - 12 Ç 25 DQ 1,050 850 800 water-cooled 130 - - - 13 Ç 35 DQ 1,050 880 820 water-cooled 100 - - - 14 D 19 RQ 1,100 870 - air-cooled - 910 water-cooled 170 15 D 25 RQ 1,100 890 - air-cooled - 910 water-cooled 170 16 D 35 DQ 1,100 890 870 water-cooled 100 - - - 17 AND 19 RQ 1,100 870 - air-cooled - 910 water-cooled 260
    32/51
    Petition 870190051900, of 6/3/2019, p. 35/61
    Steel Plate Number Steel Number Plate Thickness (mm) Treatment Type * Hot rolling DQ RQ Reheat Temperature(° C) Lamination termination temperature (° C) Cooling Start Temperature (° C) Cooling After Lamination Cooling Interruption Temperature(° C) Heating Temperature (° C) Cooling Method Cooling Interruption Temperature (° C) 18 AND 25 RQ 1,100 890 - air-cooled - 910 water-cooled 160 19 F 35 DQ 1,100 890 870 water-cooled 150 - - - 20 F 19 RQ 1,100 870 - air-cooled - 910 water-cooled 160
    33/51
    Petition 870190051900, of 6/3/2019, p. 36/61
    TABLE 2-1 (CONTINUED)
    Steel Plate Number Steel Number Plate Thickness (mm) Treatment Type * Hot rolling DQ RQ Reheat temperature (° C) Lamination termination temperature (° C) Cooling start temperature (° C) Cooling After Lamination Cooling Interruption Temperature (° C) Heating Temperature (° C) Cooling Method Cooling Interruption Temperature (° C) 21 F 25 RQ 1,100 890 - air-cooled - 910 water-cooled 160 22 G 35 DQ 1,100 890 870 water-cooled 150 - - - 23 G 19 RQ 1,100 870 - air-cooled - 910 water-cooled 280 24 G 25 RQ 1,100 890 - air-cooled - 910 water-cooled 180 25 G 35 DQ 1,100 890 870 water-cooled 150 - - - 26 H 6 RQ 1,120 910 - air-cooled - 880 water-cooled 150 27 H 19 RQ 1,120 930 - air-cooled - 900 water-cooled 150 28 H 32 DQ 1,120 870 800 water-cooled 170 - - - 29 I 6 RQ 1,120 850 - air-cooled - 950 water-cooled 150
    34/51
    Petition 870190051900, of 6/3/2019, p. 37/61
    Steel Plate Number Steel Number Plate Thickness (mm) Treatment Type * Hot rolling DQ RQ Reheat temperature ( O C) Lamination termination temperature (° C) Cooling start temperature (° C) Cooling After Lamination Cooling Interruption Temperature (° C) Heating Temperature (° C) Cooling Method Cooling Interruption Temperature ( O C) 30 I 12 RQ 1,120 860 - air-cooled - 870 water-cooled 150 31 I 19 DQ 1,120 890 830 water-cooled 150 - - - 32 J 12 RQ 1,110 860 - air-cooled - 870 water-cooled 150 33 J 19 DQ 1,110 870 840 water-cooled 170 - - - 34 J 35 DQ 1,110 880 850 water-cooled 170 - - - 35 K 6 RQ 1,120 840 - air-cooled - 930 water-cooled 150 36 K 12 RQ 1,120 870 - air-cooled - 900 water-cooled 150 37 K 20 DQ 1,120 890 830 water-cooled 180 - - -
    35/51 * DQ: direct temper, RQ: reheat temper
    Petition 870190051900, of 6/3/2019, p. 38/61
    TABLE 2-2
    Steel Plate Number Steel Number Plate Thickness(mm) Treatment Type * Hot rolling DQ RQ Reheat Temperature (° C) Rolling End Temperature (° C) Cooling Start Temperature (° C) Cooling After Lamination Cooling Interruption Temperature (° C) Heating Temperature(° C) Cooling Method Cooling Interruption Temperature(° C) 38 L 20 DQ 1,150 920 880 water-cooled 180 - - - 39 L 25 RQ 1,150 930 - air-cooled - 900 water-cooled 150 40 L 35 DQ 1,150 910 870 water-cooled 180 - - - 41 M 12 DQ 1,170 900 860 water-cooled 160 - - - 42 M 25 DQ 1,170 920 880 water-cooled 140 - - - 43 M 35 RQ 1,170 880 - air-cooled - 900 water-cooled 250 44 N 12 RQ 1,080 890 - air-cooled - 930 water-cooled 160 45 N 19 DQ 1,080 870 830 water-cooled 100 - - -
    36/51
    Petition 870190051900, of 6/3/2019, p. 39/61
    Steel Plate Number Steel Number Plate Thickness (mm) Treatment Type * Hot rolling DQ RQ Reheat Temperature (° C) Rolling End Temperature (° C) Cooling Start Temperature ( O C) Cooling After Lamination Cooling Interruption Temperature (° C) Heating Temperature ( O C) Cooling Method Cooling Interruption Temperature(° C) 46 N 25 DQ 1,080 850 810 water-cooled 120 - - - 47 O 12 RQ 1,180 840 - air-cooled - 900 water-cooled 280 48 O 19 RQ 1,180 930 - air-cooled - 930 water-cooled 280 49 O 30 DQ 1,180 900 850 water-cooled 250 - - - 50 P 6 DQ 1,150 880 840 water-cooled 250 - - - 51 P 19 DQ 1,150 840 820 water-cooled 250 - - - 52 P 35 DQ 1,150 820 800 water-cooled 250 - - - 53 Q 19 RQ 1,130 930 - air-cooled - 900 water-cooled 320 54 Q 25 DQ 1,130 920 890 water-cooled 280 - - -
    L9 / ZS
    Petition 870190051900, of 6/3/2019, p. 40/61
    Steel Plate Number Steel Number Plate Thickness (mm) Treatment Type * Hot rolling DQ RQ Reheat Temperature (° C) Rolling End Temperature (° C) Cooling Start Temperature ( O C) Cooling After Lamination Cooling Interruption Temperature (° C) Heating Temperature ( O C) Cooling Method Cooling Interruption Temperature(° C) 55 Q 35 DQ 1,130 850 830 water-cooled 280 - - - 56 R 12 RQ 1,200 860 - air-cooled - 900 water-cooled 310 57 R 25 RQ 1,200 890 - air-cooled - 900 water-cooled 290
    38/51
    Petition 870190051900, of 6/3/2019, p. 41/61
    TABLE 2-2 (CONTINUED)
    Steel Plate Number Steel Number Plate Thickness (mm) Treatment Type * Hot Rolling Mill DQ RQ Reheat Temperature(° C) Rolling End Temperature (° C) Cooling Start Temperature (° C) Cooling After Lamination Cooling Interruption Temperature (° C) Heating Temperature(° C) Cooling Method Cooling Interruption Temperature(° C) 58 R 35 DQ 1,200 880 840 water-cooled 300 - - - 59 s 6 RQ 1,120 850 - air-cooled - 880 water-cooled 210 60 s 19 DQ 1,120 870 830 water-cooled 300 - - - 61 s 35 RQ 1,120 900 - air-cooled - 850 water-cooled 210 62 T 12 RQ 1,120 920 - air-cooled - 920 water-cooled 150 63 T 25 RQ 1,120 900 - air-cooled - 900 water-cooled 150 64 T 32 RQ 1,120 880 - air-cooled - 870 water-cooled 150 65 U 12 RQ 1,180 900 - air-cooled - 890 water-cooled 150
    39/51
    Petition 870190051900, of 6/3/2019, p. 42/61
    Steel Plate Number Steel Number Plate Thickness (mm) Treatment Type * Hot Rolling Mill DQ RQ Reheat Temperature ( O C) Rolling End Temperature ( O C) Cooling Start Temperature ( O C) Cooling After Lamination Cooling Interruption Temperature (° C) Heating Temperature ( O C) Cooling Method Cooling Interruption Temperature(° C) 66 U 19 DQ 1,180 880 850 water-cooled 150 - - - 67 U 32 RQ 1,180 890 - air-cooled - 870 water-cooled 180 68 V 12 RQ 1,120 870 - air-cooled - 920 water-cooled 180 69 V 25 RQ 1,120 930 - air-cooled - 910 water-cooled 180 70 V 32 RQ 1,120 900 - air-cooled - 920 water-cooled 180 71 W 12 DQ 1,180 860 830 water-cooled 150 - - - 72 W 19 RQ 1,180 900 - air-cooled - 900 water-cooled 190 73 W 32 RQ 1,180 910 - air-cooled - 870 water-cooled 190
    40/51 * DQ: direct temper, RQ: reheat temper
    Petition 870190051900, of 6/3/2019, p. 43/61
    TABLE 2-3
    Steel Plate Number Steel Number Plate Thickness(mm) Treatment Type * Hot rolling DQ RQ Cooling rate in Water Cooling800 ° C ^ 500 ° C (° C / s) Comments Reheat Temperature ( O C) Rolling End Temperature ( O C) Cooling Start Temperature (° C) Cooling After Lamination Cooling Interruption Temperature ( O C) Heating Temperature ( O C) Cooling Method Temp. Cooling Interrupt ( O C) 74 THE 12 RQ 1,120 900 - air-cooled - 900 water-cooled 150 32 example of the present invention 75 THE 12 RQ 1,120 900 - air-cooled - 910 water-cooled 150 28 example of the present invention 76 THE 12 RQ 1,120 900 - air-cooled - 900 water-cooled 150 62 example of the present invention 77 THE 12 DQ 1,120 880 860 water-cooled 145 - - - 65 example of the present invention 78 THE 12 DQ 1,120 870 850 water-cooled 150 - - - 71 example of the present invention 79 THE 19 RQ 1,120 920 - air-cooled - 910 water-cooled 170 19 example of the present invention
    41/51
    Petition 870190051900, of 6/3/2019, p. 44/61
    Steel Plate Number Steel Number Plate Thickness (mm) Treatment Type * Hot rolling DQ RQ Cooling rate in Water Cooling800 ° C-> 500 ° C (° C / s) Comments Reheat Temperature(° C) Rolling End Temperature (° C) Cooling Start Temperature (° C) Cooling After Lamination Cooling Interruption Temperature (° C) Heating Temperature(° C) Cooling Method Temp. Cooling Interrupt(° C) 80 THE 19 RQ 1120 920 - air-cooled - 900 water-cooled 150 19 example of the present invention 81 THE 19 DQ 1120 890 840 water-cooled 150 - - - 41 example of the present invention 82 THE 25 DQ 1120 880 830 water-cooled 150 - - - 15 example of the present invention 83 THE 25 RQ 1,120 890 - air-cooled - 900 water-cooled 150 32 example of the present invention 84 B 12 RQ 1,120 890 - air-cooled - 900 water-cooled 150 32 example of the present invention 85 B 12 RQ 1,120 890 - air-cooled - 900 water-cooled 160 65 example of the present invention
    42/51
    Petition 870190051900, of 6/3/2019, p. 45/61
    Steel Plate Number Steel Number Plate Thickness (mm) Treatment Type * Hot rolling DQ RQ Cooling rate in Water Cooling800 ° C-> 500 ° C (° C / s) Comments Reheat Temperature(° C) Rolling End Temperature (° C) Cooling Start Temperature (° C) Cooling After Lamination Cooling Interruption Temperature (° C) Heating Temperature(° C) Cooling Method Temp. Cooling Interrupt(° C) 86 B 12 DQ 1,120 950 890 water-cooled 150 - - - 71 example of the present invention 87 B 19 DQ 1,120 870 850 water-cooled 150 - - - 19 example of the present invention 88 B 19 DQ 1,120 950 890 water-cooled 150 - - - 40 example of the present invention 89 B 32 DQ 1,120 890 840 water-cooled 150 - - - 12 example of the present invention
    43/51 * DQ: direct temper, RQ: reheat temper
    Petition 870190051900, of 6/3/2019, p. 46/61
    44/51
    TABLE 3-1
    Steel Plate Number Steel Number Structure Surface Hardness Low temperature toughness Resistance to corrosive wear Comments Grain size ofPrevious Austenite grains (pm) Martensitic fraction (area%) HBW 10/3000 vE-40 (° C) Wear resistance ratio (Reference: 1.0 (conventional example)) 1 THE 25 93 486 33 1.5 example of the present invention 2 THE 27 92 491 32 1.5 example of the present invention 3 THE 27 91 493 31 1.5 example of the present invention 4 THE 28 85 432 30 1.3 example for comparison 5 THE 32 83 430 17 1.2 example for comparison 6 B 22 96 469 38 1.9 example of the present invention 7 B 25 93 468 34 1.9 example of the present invention 8 B 26 92 459 33 1.9 example of the present invention 9 B 36 92 466 17 1.9 example for comparison 10 B 35 94 471 14 2.0 example for comparison 11 Ç 16 97 465 39 1.9 example of the present invention 12 Ç 18 95 469 36 2.0 example of the present invention 13 Ç 19 93 472 34 2.1 example of the present invention 14 D 15 95 455 45 2.0 example of the present invention
    Petition 870190051900, of 6/3/2019, p. 47/61
    45/51
    Steel Plate Number Steel Number Structure Surface Hardness Low temperature toughness Resistance to corrosive wear Comments Grain size ofPrevious Austenite grains (pm) Martensitic fraction (area%) HBW10/3000 vE-40 (° C) Wear resistance ratio (Reference: 1.0 (conventional example)) 15 D 12 96 460 46 2.1 example of the present invention 16 D 10 94 465 50 2.3 example of the present invention 17 AND 15 95 470 45 2.0 example of the present invention 18 AND 14 96 475 46 2.1 example of the present invention 19 F 12 94 490 52 2.4 example of the present invention 20 F 16 95 470 42 2.0 example of the present invention 21 F 13 95 489 46 2.1 example of the present invention 22 G 12 94 498 47 2.0 example of the present invention 23 G 18 94 470 46 2.0 example of the present invention 24 G 17 93 478 45 2.1 example of the present invention 25 G 15 95 498 48 2.1 example of the present invention 26 H 25 95 515 35 1.5 example of the present invention 27 H 27 93 519 33 1.5 example of the present invention 28 H 28 91 521 32 1.5 example of the present invention 29 I 22 96 493 33 1.6 example of the present invention
    Petition 870190051900, of 6/3/2019, p. 48/61
    46/51
    Steel Plate Number Steel Number Structure Surface Hardness Low temperature toughness Resistance to corrosive wear Comments Grain size ofPrevious Austenite grains (pm) Martensitic fraction (area%) HBW10/3000 vE-40 (° C) Wear resistance ratio (Reference: 1.0 (conventional example)) 30 I 24 94 503 36 1.6 example of the present invention 31 I 25 92 505 32 1.6 example of the present invention 32 J 21 97 521 38 2.0 example of the present invention 33 J 17 95 534 40 2.1 example of the present invention 34 J 16 93 539 42 2.0 example of the present invention 35 K 23 96 465 36 2.1 example of the present invention 36 K 20 93 470 37 2.1 example of the present invention 37 K 24 92 481 34 2.1 example of the present invention
    Petition 870190051900, of 6/3/2019, p. 49/61
    47/51
    TABLE 3-2
    Steel Plate Number Steel Number Structure Surface Hardness Low Temperature Toughness Resistance to corrosive wear Comments Grain size ofPrevious Austenite grains (pm) Martensitic fraction (% of area) HBW 10/3000 vE-40 (° C) Wear resistance ratio (Reference: 1.0 (conventional example)) 38 L 12 97 557 49 2.4 example of the present invention 39 L 13 95 545 57 2.4 example of the present invention 40 L 13 93 550 52 2.4 example of the present invention 41 M 11 93 508 45 1.6 example of the present invention 42 M 12 94 512 42 1.6 example of the present invention 43 M 10 92 505 45 1.5 example of the present invention 44 N 13 99 490 73 2.5 example of the present invention 45 N 10 98 493 62 2.5 example of the present invention 46 N 8 97 488 66 2.5 example of the present invention 47 O 32 92 482 27 0.8 example for comparison 48 O 34 91 491 25 0.8 example for comparison 49 O 31 93 493 24 0.8 example for comparison 50 P 38 95 531 17 0.9 example for comparison 51 P 36 92 524 22 0.9 example for comparison
    Petition 870190051900, of 6/3/2019, p. 50/61
    48/51
    Steel Plate Number Steel Number Structure Surface Hardness Low TenacityTemperature Resistance to corrosive wear Comments Grain size ofPrevious Austenite grains (pm) Martensitic fraction (% of area) HBW10/3000 vE-40 ( O C) Wear resistance ratio (Reference: 1.0 (conventional example)) 52 P 32 93 519 24 0.9 example for Comparation 53 Q 33 94 521 28 1.2 example forComparation 54 Q 32 92 532 25 1.2 example forComparation 55 Q 34 92 530 27 1.2 example forComparation 56 R 15 96 413 51 1.4 example for Comparation 57 R 16 93 410 48 1.4 example for Comparation 58 R 16 91 409 44 1.4 example for Comparation 59 s 22 52 420 15 1.2 example forComparation 60 s 21 55 425 20 1.2 example forComparation 61 s 25 47 413 12 1.2 example forComparation 62 T 27 94 507 34 1.6 example of the present invention 63 T 26 94 509 36 1.6 example of the present invention 64 T 25 93 506 37 1.6 example of the present invention 65 U 23 96 511 37 2.1 example of the present invention 66 U 26 95 510 35 2.1 example of the present invention
    Petition 870190051900, of 6/3/2019, p. 51/61
    49/51
    Steel Plate Number Steel Number Structure Surface Hardness Low TenacityTemperature Resistance to corrosive wear Comments Grain size ofPrevious Austenite grains (pm) Martensitic fraction (% of area) HBW10/3000 vE-40 ( O C) Wear resistance ratio (Reference: 1.0 (conventional example)) 67 U 22 96 507 40 2.1 example of the present invention 68 V 20 97 520 40 2.4 example of the present invention 69 V 19 96 523 43 2.4 example of the present invention 70 V 21 97 519 38 2.5 example of the present invention 71 W 21 97 528 45 2.4 example of the present invention 72 W 17 97 531 48 2.4 example of the present invention 73 W 15 96 521 51 2.4 example of the present invention
    Petition 870190051900, of 6/3/2019, p. 52/61
    50/51
    TABLE 3-3
    Steel Plate Number Steel Number Structure Surface Hardness Low temperature toughness Resistance to corrosive wear Comments Grain size ofPrevious Austenite grains (pm) Martensitic fraction (% of area) HBW 10/3000 vE-40 (° C) Wear resistance ratio (Reference: 1.0 (conventional example)) 74 THE 25 93 486 33 1.5 example of the present invention 75 THE 27 94 493 34 1.5 example of the present invention 76 THE 26 97 500 32 1.6 example of the present invention 77 THE 25 98 501 31 1.7 example of the present invention 78 THE 26 99 504 32 1.8 example of the present invention 79 THE 27 92 491 32 1.5 example of the present invention 80 THE 27 92 492 33 1.5 example of the present invention 81 THE 26 96 498 34 1.6 example of the present invention 82 THE 27 91 493 31 1.5 example of the present invention 83 THE 26 95 496 30 1.7 example of the present invention 84 B 22 96 469 38 1.9 example of the present invention 85 B 21 98 473 39 2.0 example of the present invention 86 B 20 99 477 38 2.1 example of the present invention 87 B 25 93 468 34 1.9 example of the present invention
    Petition 870190051900, of 6/3/2019, p. 53/61
    51/51
    Steel Plate Number Steel Number Structure Surface Hardness Low temperature toughness Resistance to corrosive wear Comments Grain size ofPrevious Austenite grains (pm) Martensitic fraction (% of area) HBW10/3000 vE-40 (° C) Wear resistance ratio (Reference: 1.0 (conventional example)) 88 B 25 96 472 36 2.0 example of the present invention 89 B 26 92 459 33 1.9 example of the present invention
    [0094] All examples of the present invention exhibit high surface hardness of 450 or greater in HBW 10/3000, excellent tenacity at low temperature of vE-40 of 30 J or greater and excellent corrosion wear resistance of the wear resistance ratio in
    1.5 or more. In addition, the chilled steel plate with a higher cooling rate has a higher martensitic fraction. In particular, the steel plate that has a martensitic fraction of 98% or more exhibits excellent resistance to corrosive wear in particular, when compared to the steel plate that has a martensitic fraction of less than 98% and that has the same composition. On the other hand, comparative examples that are outside the scope of the present invention exhibit decreased surface hardness, decreased toughness at low temperature, decreased resistance to corrosive wear or decreased two or more of these properties.
    权利要求:
    Claims (6)
    [1]
    claims
    1. Abrasion resistant steel plate, characterized by the fact that it presents excellent tenacity at low temperature and excellent resistance to corrosive wear, and the steel plate has the composition containing in% by mass:
    0.23% to 0.35% C,
    0.05% to 1.00% Si,
    0.1% to 2.0% Mn,
    0.020% or less of P,
    0.005% or less of S,
    0.005% to 0.100% Al,
    0.03% to 2.0% Cr, and
    0.03% to 1.0% Mo;
    in a state in which DI * defined by the following formula (1) is satisfied as 45 or more and still contains Fe remaining and unavoidable impurities as a balance, the steel plate having a structure in which a martensitic phase in the condition tempered forms a main phase and a grain size of previous austenite grains is 30 pm or less, and the surface hardness of the steel plate is 450 or greater in Brinel HBW10 / 3000 hardness.
    FORMULA DI * = 33.85x (0.1xC) 0 ' 5 x (0.7xSi + 1) x (3.33xMn + 1) x (0.35xCu + 1) x (0.36xNi +1) x (2 , 16xCr + 1) x (3xMo + 1) x (1,75xV + 1) (1) (where, C, Si, Mn, Cu, Ni, Cr, Mo and V in formula (1) refer to the contents (% by mass) of the respective elements).
    [2]
    2. Abrasion-resistant steel plate according to claim 1, characterized by the fact that the steel composition also contains, in% by mass, one or two or more types of components selected from a group consisting of :
    0.005% to 0.1% Nb,
    Petition 870190051900, of 6/3/2019, p. 55/61
    2/2
    0.005% to 0.1% Ti, and
    0.005% to 0.1% of V.
    [3]
    3. Abrasion-resistant steel plate according to claim 1 or 2, characterized by the fact that the steel composition also contains, in% by weight, one or two types of components selected from a group consisting of :
    0.005% to 0.2% of Sn, and
    0.005% to 0.2% Sb.
    [4]
    4. Abrasion-resistant steel plate according to any one of claims 1 to 3, characterized by the fact that the steel composition also contains, in mass%, one or two or more types of components selected from a group that consisting of:
    0.03% to 1.0% Cu,
    0.03% to 2.0% Ni, and
    0.0003% to 0.0030% B.
    [5]
    Abrasion-resistant steel plate according to any one of claims 1 to 4, characterized by the fact that the steel composition also contains, in mass%, one or two or more types of components selected from a group consisting of:
    0.0005% to 0.008% of REM,
    0.0005% to 0.005% Ca, and
    0.0005% to 0.005% Mg.
    [6]
    6. Abrasion-resistant steel plate according to any one of claims 1 to 5, characterized by the fact that the content of the martensitic phase in the tempered condition is 98% or more in terms of volume fraction.
    类似技术:
    公开号 | 公开日 | 专利标题
    BR112015005951B1|2019-09-17|ABRASION RESISTANT STEEL PLATE WITH EXCELLENT LOW TEMPERATURE AND EXCELLENT RESISTANCE TO CORROSIVE WEAR
    BR112015005986B1|2019-08-13|abrasion resistant steel plate which has excellent low temperature toughness and excellent corrosive wear resistance
    EP2881482B1|2019-07-24|Wear resistant steel plate and manufacturing process therefor
    BR112015020012B1|2020-11-17|ABRASION-RESISTANT STEEL PLATE THAT HAS LOW TEMPERATURE TENACITY AND RESISTANCE TO HYDROGEN FRAGILIZATION AND METHOD FOR MANUFACTURING THE SAME
    EP3597784B1|2021-03-31|Abrasion-resistant steel plate and method of manufacturing same
    ES2734993T3|2019-12-13|High strength steel material for use in oil wells, and oil well pipes
    BR112015020046B1|2020-05-05|abrasion-resistant thick steel plate with excellent low temperature stiffness and manufacturing method
    BR122017002730B1|2018-02-06|METHOD OF PRODUCTION OF A HIGH RESISTANCE STEEL SHEET
    BR112016017304B1|2021-01-05|abrasion resistant steel plate and method for producing the same
    BR112018012400B1|2020-02-18|STAINLESS STEEL TUBE WITHOUT HIGH-RESISTANCE SEWING FOR OIL WELLS AND THE MANUFACTURING METHOD OF THE SAME
    BRPI0905378B1|2017-06-27|HIGH RESISTANCE STEEL SHEET
    JP6245220B2|2017-12-13|Abrasion resistant steel plate with excellent low temperature toughness and corrosion wear resistance
    JP6217585B2|2017-10-25|Abrasion resistant steel plate excellent in bending workability and impact wear resistance and method for producing the same
    JP2015193873A|2015-11-05|Thick steel plate excellent in abrasion resistance in corrosive environment
    BR112016001817B1|2021-04-06|THICK STEEL PLATE AND METHOD FOR MANUFACTURING THE SAME
    ES2769257T3|2020-06-25|Aging-curable steel, and method of manufacturing components including aging-curable steel
    JP6217586B2|2017-10-25|Abrasion resistant steel plate excellent in bending workability and impact wear resistance and method for producing the same
    JP6164193B2|2017-07-19|Abrasion resistant steel plate excellent in bending workability and impact wear resistance and method for producing the same
    BRPI0901014B1|2017-08-15|WEAVING STEEL PLATE AND METHOD FOR PRODUCING THE SAME
    同族专利:
    公开号 | 公开日
    EP2873748A4|2015-10-28|
    EP2873748B1|2018-03-14|
    CN104685088A|2015-06-03|
    EP2873748A1|2015-05-20|
    MX2015003379A|2015-06-05|
    PE20150790A1|2015-05-30|
    CL2015000661A1|2015-08-21|
    JPWO2014045552A1|2016-08-18|
    KR20150038590A|2015-04-08|
    AU2013319621A1|2015-02-26|
    BR112015005951A2|2017-07-04|
    IN2015DN00771A|2015-07-03|
    WO2014045552A1|2014-03-27|
    US20150232971A1|2015-08-20|
    AU2013319621B2|2016-10-13|
    引用文献:
    公开号 | 申请日 | 公开日 | 申请人 | 专利标题
    JPH0371499B2|1985-01-18|1991-11-13|Sumitomo Kinzoku Kogyo Kk|
    JPH02179842A|1988-12-29|1990-07-12|Sumitomo Metal Ind Ltd|High-toughness wear-resistant steel sheet|
    JPH0841535A|1994-07-29|1996-02-13|Nippon Steel Corp|Production of high hardness wear resistant steel excellent in low temperature toughness|
    JP2002020837A|2000-07-06|2002-01-23|Nkk Corp|Wear resistant steel excellent in toughness and its production method|
    JP4650013B2|2004-02-12|2011-03-16|Ｊｆｅスチール株式会社|Abrasion resistant steel plate with excellent low temperature toughness and method for producing the same|
    JP4735167B2|2005-09-30|2011-07-27|Ｊｆｅスチール株式会社|Method for producing wear-resistant steel sheet with excellent low-temperature toughness|
    JP5017937B2|2005-12-28|2012-09-05|Ｊｆｅスチール株式会社|Wear-resistant steel plate with excellent bending workability|
    JP5145804B2|2007-07-26|2013-02-20|Ｊｆｅスチール株式会社|Abrasion-resistant steel plate with excellent low-temperature tempering embrittlement cracking properties|
    JP5145803B2|2007-07-26|2013-02-20|Ｊｆｅスチール株式会社|Wear-resistant steel plate with excellent low-temperature toughness and low-temperature tempering embrittlement cracking properties|
    JP5145805B2|2007-07-26|2013-02-20|Ｊｆｅスチール株式会社|Wear-resistant steel plate with excellent gas cut surface properties and low-temperature tempering embrittlement cracking resistance|
    CN101855379B|2008-10-27|2012-07-25|新日本制铁株式会社|Fire-resistant steel material with excellent resistance to reheat embrittlement and with low-temperature toughness at welded heat-affected parts, and manufacturing method thereof|
    JP5655356B2|2010-04-02|2015-01-21|Ｊｆｅスチール株式会社|Wear-resistant steel plate with excellent low-temperature temper embrittlement cracking|
    JP5866820B2|2010-06-30|2016-02-24|Ｊｆｅスチール株式会社|Wear-resistant steel plate with excellent weld toughness and delayed fracture resistance|
    KR20120071615A|2010-12-23|2012-07-03|주식회사 포스코|Wear resistant steel plate having excellent low-temperature toughness and weldability, and method for manufacturing the same|
    KR101271888B1|2010-12-23|2013-06-05|주식회사 포스코|Thick Plate Having Excellent Wear Resistant And Low-Temperature Toughness, And Method For Manufacturing The Same|
    JP5683327B2|2011-03-07|2015-03-11|Ｊｆｅスチール株式会社|Wear-resistant steel plate with excellent low-temperature toughness|
    PE20141712A1|2011-03-29|2014-11-28|Jfe Steel Corp|ABRASION RESISTANT STEEL PLATE OR STEEL SHEET THAT HAS EXCELLENT STRESS RESISTANCE TO CORROSION CRACKING AND METHOD OF MANUFACTURING IT|
    CN103459634B|2011-03-29|2015-12-23|杰富意钢铁株式会社|The wear-resistant steel plate of anticorrosion stress-resistant breaking property excellence and manufacture method thereof|
    CN102492896A|2011-12-29|2012-06-13|钢铁研究总院|Steel for upper deck of cargo oil tank of tanker|JP6235221B2|2013-03-28|2017-11-22|Ｊｆｅスチール株式会社|Wear-resistant thick steel plate having low temperature toughness and hydrogen embrittlement resistance and method for producing the same|
    US10662493B2|2014-01-28|2020-05-26|Jfe Steel Corporation|Abrasion-resistant steel plate and method for manufacturing the same|
    JP6232324B2|2014-03-24|2017-11-15|Ｊｆｅスチール株式会社|Stabilizer steel and stabilizer with high strength and excellent corrosion resistance, and method for producing the same|
    JP6394378B2|2014-12-26|2018-09-26|新日鐵住金株式会社|Abrasion resistant steel sheet and its manufacturing method |
    CN104818437B|2015-03-27|2017-05-31|上海材料研究所|A kind of self-lubricating antifriction wear-resisting alloy steel and preparation method thereof|
    JP6245220B2|2015-05-29|2017-12-13|Ｊｆｅスチール株式会社|Abrasion resistant steel plate with excellent low temperature toughness and corrosion wear resistance|
    CN104988413A|2015-06-17|2015-10-21|柳州金特新型耐磨材料股份有限公司|Bucket tooth|
    CN104911500B|2015-06-26|2017-01-11|龙岩盛丰机械制造有限公司|Manufacturing method of low-temperature wear-resistant carriage|
    CN104988290A|2015-08-11|2015-10-21|内蒙古包钢钢联股份有限公司|Heat treatment method for steel for high-hardenability and wear-resisting bucket teeth|
    CN105002441A|2015-08-11|2015-10-28|内蒙古包钢钢联股份有限公司|Steel for high-hardenability wear-resistant bucket teeth|
    CN105154783A|2015-08-12|2015-12-16|宁波东灵水暖空调配件有限公司|Adjusting mechanism for electric air valve|
    KR101696094B1|2015-08-21|2017-01-13|주식회사 포스코|Steel sheet having superior hardness and method for manufacturing the same|
    CN105063497B|2015-09-17|2017-10-17|东北大学|A kind of high-wear resistance easy processing low alloy wear resistance steel plate and its manufacture method|
    KR101736621B1|2015-12-15|2017-05-30|주식회사 포스코|High hardness anti-abrasion steel having excellent toughness and superior resistance to cracking during thermal cutting|
    CN105648342A|2016-02-26|2016-06-08|铜陵安东铸钢有限责任公司|Wear-resistant high-chromium steel and manufacturing method thereof|
    BR112018068935A2|2016-04-19|2019-01-22|Jfe Steel Corp|abrasion resistant steel sheet and method for producing abrasion resistant steel sheet|
    EP3446809B1|2016-04-19|2020-06-10|JFE Steel Corporation|Abrasion-resistant steel plate and method for producing abrasion-resistant steel plate|
    CN108884531B|2016-04-19|2020-06-19|杰富意钢铁株式会社|Wear-resistant steel sheet and method for producing wear-resistant steel sheet|
    JP6119935B1|2016-04-19|2017-04-26|Ｊｆｅスチール株式会社|Abrasion resistant steel sheet and method for producing the abrasion resistant steel sheet|
    CN105734424A|2016-05-09|2016-07-06|周常|Alloy material for offshore drilling platform freshwater cooling system and preparation method thereof|
    CN106119725A|2016-05-09|2016-11-16|林淑录|A kind of marine drilling platform fuel system alloy material and preparation method thereof|
    CN106282787B|2016-08-09|2018-04-17|卢森加|A kind of manufacture method of cast steel material and its casting|
    CN109504903B|2016-08-18|2021-01-29|江苏鼎泰工程材料有限公司|Low-alloy ultrahigh-strength steel|
    KR101899686B1|2016-12-22|2018-10-04|주식회사 포스코|Wear resistant steel havinh high hardness and method for manufacturing the same|
    CN108034888B|2017-12-13|2020-05-08|张旭峰|Alloy steel for integrally forging frog and heat treatment process thereof|
    KR102031446B1|2017-12-22|2019-11-08|주식회사 포스코|Wear resistant steel having excellent hardness and impact toughness and method of manufacturing the same|
    JP6477983B1|2018-03-29|2019-03-06|新日鐵住金株式会社|Austenitic wear-resistant steel sheet|
    EA201891069A1|2018-05-30|2019-12-30|РЕЙЛ 1520 АйПи ЛТД.|ALLOY CASTING STEEL AND PRODUCTS FROM IT|
    KR102175570B1|2018-09-27|2020-11-06|주식회사 포스코|Wear resistant steel having excellent hardness and impact toughness and method of manufacturing the same|
    KR102119959B1|2018-09-27|2020-06-05|주식회사 포스코|Wear resistant steel having excellent hardness and impact toughness and method of manufacturing the same|
    CN109881092B|2019-02-26|2021-11-16|舞阳钢铁有限责任公司|Large-thickness rack steel plate and production method thereof|
    CN110387507B|2019-08-09|2021-04-06|武汉钢铁有限公司|HB500 grade wear-resistant steel for corrosive slurry transport container and production method thereof|
    CN111363974A|2020-03-24|2020-07-03|马鞍山钢铁股份有限公司|Niobium-vanadium-containing axle for urban rail subway and heat treatment process thereof|
    CN111826586A|2020-06-15|2020-10-27|舞阳钢铁有限责任公司|Low-cost large-thickness rack steel and production method thereof|
    CN113684427A|2021-08-13|2021-11-23|北京首钢冷轧薄板有限公司|800 MPa-grade dual-phase steel with excellent bulging capacity and preparation method thereof|
    法律状态:
    2018-11-21| B06F| Objections, documents and/or translations needed after an examination request according [chapter 6.6 patent gazette]|
    2019-03-06| B06A| Patent application procedure suspended [chapter 6.1 patent gazette]|
    2019-07-30| B09A| Decision: intention to grant [chapter 9.1 patent gazette]|
    2019-09-17| B16A| Patent or certificate of addition of invention granted [chapter 16.1 patent gazette]|Free format text: PRAZO DE VALIDADE: 20 (VINTE) ANOS CONTADOS A PARTIR DE 13/09/2013, OBSERVADAS AS CONDICOES LEGAIS. (CO) 20 (VINTE) ANOS CONTADOS A PARTIR DE 13/09/2013, OBSERVADAS AS CONDICOES LEGAIS |
    优先权:
    申请号 | 申请日 | 专利标题
    JP2012205304|2012-09-19|
    JP2012-205304|2012-09-19|
    PCT/JP2013/005433|WO2014045552A1|2012-09-19|2013-09-13|Wear-resistant steel plate having excellent low-temperature toughness and corrosion wear resistance|
    [返回顶部]