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    patent summary: "abrasion resistant steel plate which has excellent low temperature toughness and excellent corrosive wear resistance". The present invention relates to an abrasion resistant steel plate which has excellent low temperature toughness and corrosive wear resistance. an abrasion resistant steel plate having excellent low temperature toughness and corrosive wear resistance containing by weight 0.10% to 0.20% of c, 0.05% to 1.00% of itself, 0 , 1% to 2,0% of mn, not more than 0,020% of p, not more than 0,005% of s and 0,005% to 0,100% of al, and additionally containing one or two element types selected from 0,05% at 2.0% cr and 0.05% to 1.0% by hand, and satisfying the condition that the amount of steel solid solution (crsol) content and the amount of solid solution hand content of steel (mosol) is 0,05? (crsol + 2.5 mosol)? 2.0 having a component structure comprising a remainder of unavoidable faith and impurities using a martensite phase in the cooled condition as a main phase having a structure in which the previous austenite grain size is not is greater than 30 µm, and additionally having surface hardness being at least 360 in terms of a brinel hardness of hbw10 / 3000.
    公开号:BR112015005986B1
    申请号:R112015005986
    申请日:2013-09-13
    公开日:2019-08-13
    发明作者:Ueda Keiji；Ishikawa Nobuyuki；Miura Shinichi
    申请人:Jfe Steel Corp；
    IPC主号:
    专利说明:

    Invention Patent Descriptive Report for ABRASION-RESISTANT STEEL PLATE THAT HAS EXCELLENT TENACITY AT LOW TEMPERATURE AND EXCELLENT RESISTANCE TO CORROSIVE WEAR.
    FIELD OF TECHNIQUE [0001] The present invention relates to an abrasion-resistant steel plate used appropriately 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 refers to an abrasion-resistant steel plate that can be used appropriately as parts that are used in places where wear and tear or the abrasion generated due to contact of the abrasion-resistant steel plate with water-containing earth and sand must be particularly taken into account.
    BACKGROUND TECHNIQUE [0002] Conventionally, in relation to parts for industrial machinery, transport machinery and the like such as, for example, an excavator, bulldozer, hopper, bucket or tipper used on a construction site, a civil engineering site, a mine or similar, wear and tear is generated due to a part's contact with the 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 earth, sand or the like in a wet state contains a corrosive material. Thus, wear due to earth, sand or the like, in a wet state, becomes wear in an environment that contains the material
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    2/45 corrosive, that is, called corrosive wear. This corrosive wear has been known as an extremely severe wear environment. In view of the above, there has been a demand for an abrasion resistant steel material that has excellent resistance to corrosive wear.
    [0003] The use of these industrial machines, transport machines and the like in a low temperature range 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.
    [0004] In order to satisfy such a requirement, for example, patent literature 1 proposes a method to manufacture 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 steel plate from a transformation point temperature of Ar3 or above and subsequently , the cooled plate is hardened, thereby obtaining high strength abrasion resistant steel. According to the description of the technique described in patent literature 1, the improvement of temperability 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, the further improvement of toughness at low temperature is achieved by applying tempering treatment to steel.
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    3/45 [0005] Patent Literature 2 proposes an abrasion-resistant steel plate of high tenacity that has the composition containing, in mass%: 0.18% to 0.25% of C, 0.10% at 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 more than 0, 50% to 0.80% Mo, and exhibits excellent toughness and excellent resistance to delayed fracture after water cooling and tempering. According to the description of a technique described in Patent Literature 2, by 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 hardenability can be improved so that predetermined hardness can be guaranteed and, at the same time, delayed fracture resistance and toughness can be improved. In addition, according to the description of the technique described in Patent Literature 2, the low temperature toughness is further improved by applying tempering additionally.
    [0006] Patent Literature 3 proposes an abrasion resistant and high tenacity steel that has the composition containing, in% by weight,: 0.30% to 0.45% of C, 0.10% to 0.50 % 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 is improved and, by At the same time, grain contours are reinforced, thereby improving low temperature toughness.
    [0007] Patent Literature 4 proposes a method to manufacture an abrasion resistant steel, in which hot rolling is applied to steel that has a composition containing, in mass%: 0.05% to 0.40% C, 0.1% to 2.0% Cr, appropriate amounts of Si, Mn,
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    Ti, B, Al and N respectively and, in addition, 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 below thereafter, the quench is applied to a hot-rolled plate from a transformation point temperature of Ar3 or above and, subsequently, the cooled plate is tempered, 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.
    [0008] 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% of Si, 0.1% to 2.0% of Mn, 0.10% to 1.40% of W, 0.0003% to 0.0020% of 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, in the technique described in Patent Literature 5, it is considered that the abrasion-resistant steel plate has high surface hardness and exhibits excellent resistance to abrasion and excellent low temperature toughness.
    [0009] Additionally, in Patent Literature 6, an abrasion resistant steel plate that has excellent bending properties is described. The abrasion-resistant steel plate described in Patent Literature 6 is an abrasion-resistant steel plate that has the
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    5/45 position containing, in mass%: 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 is formed of a ferrite phase and a hard phase is dispersed in the matrix. The abrasion-resistant steel plate 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 a composition, in the technique described in Patent Literature 6, it is considered that both abrasion resistance and curvature property against abrasion caused by soil and sand can be improved without inducing a noticeable increase in 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] However, the respective techniques described in Patent Literature 1 to 5 aim at the acquisition of steel plates that have low temperature toughness and abrasion resistance. In addition, the technique described in Patent Literature 6 aims at acquiring the steel plate which has both curvature property and abrasion resistance. However, in none of these Patent Literatures, the
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    6/45 wear in an environment that contains a corrosive material such as earth and sand in a wet state has been studied and, therefore, there is a disadvantage in which consideration has not been given to corrosive wear resistance.
    [0017] Additionally, in the respective techniques described in Patent Literature 1 to 4, tempering treatment 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, surface hardness is low, therefore, the steel plate cannot acquire sufficient abrasion resistance.
    [0018] The present invention was carried out in order to overcome the disadvantages mentioned above of the related technique and, it is an objective of the present invention to provide an abrasion resistant steel plate that can be manufactured at low cost, and has excellent resistance to abrasion , which has excellent low temperature toughness and 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 abrasion resistance, low temperature toughness and resistance to corrosive wear. 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 the composition containing appropriate amounts of Cr and / or Mo as indispensable components, and adjusting the solute content in steel and the solute content in steel are so that the following formula (1) is satisfied.
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    0.05 <(Crsol + 2.5Mosol) <2.0 ...... (1) [0020] (Here, Crsol: the content of Cr solute in steel (% by mass), Mosol: the content of steel solute Mo (% by mass)).
    [0021] It is assumed that by allowing the steel plate to contain appropriate amounts of Cr and / or Mo as indispensable components and by allowing the steel plate to ensure appropriate amounts of Cr and Mo solute, even when the steel is exposed to earth and sand in a wet state that has a pH in a wide range, Cr and / or Mo exists as an oxyacid and therefore corrosive wear is suppressed.
    [0022] The inventors also found that the abrasion resistance and the corrosive wear resistance against abrasion caused by earth and sand can be noticeably improved by maintaining the surface hardness at a high level as long as the steel plate has the composition mentioned above.
    [0023] The inventors also found that the hardness of the steel plate can be improved by allowing the steel plate to contain appropriate amounts of Cr and / or Mo as indispensable components and by adjusting the composition of the steel plate so that the steel plate contains appropriate amounts of at least C, Si, Mn, P, S and Al, in addition, the excellent tenacity at low temperature can also certainly be achieved by guaranteeing the structure in which a martensitic phase in the cooled condition forms a main phase and a previous austenite (γ) grain size is 30 gm or less.
    [0024] The present invention was carried out based on the findings mentioned above and was completed after further study of the findings. That is, the essential point of the invention is as follows.
    [0025] (1) An abrasion resistant steel plate that has excellent low temperature toughness and excellent resistance to de
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    8/45 wear corrosive, the steel plate that has a composition containing, in mass%: 0.10% to 0.20% 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, one or two types of components selected from a group consisting of 0.05% to 2 , 0% Cr and 0.05% to 1.0% Mo, and Fe remaining and unavoidable impurities as an equilibrium, where the content of Cr solute in steel and the content of Sol sol Mo in steel satisfy the following formula ( 1), the steel plate which has a structure in which a martensitic phase in the cooled condition forms a main phase and a grain size of previous austenite grains is 30 qm or less, and the surface hardness of the steel plate is 360 or more in Brinel HBW10 / 3000 hardness.
    0.05 <(Crsol + 2.5Mosol) <2.0 ... (1) [0026] where, Crsol: the solute content Cr in steel (% by mass), Mosol: the solute content Mo in steel (mass%) [0027] (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.
    [0028] (3) In the abrasion-resistant steel plate described in (1) or (2), the steel composition additionally 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% of Sb.
    [0029] (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.
    [0030] (5) On the abrasion-resistant steel plate described in which
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    9/45 or one of (1) to (4), the steel composition additionally contains, in mass%, 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.
    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 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 decreasing 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 are explained. In the explanation given below, mass% is simply expressed by% unless otherwise specified.
    C: 0.10% to 0.20% [0033] C is an important element to increase the hardness of the steel plate and to improve the abrasive resistance. When the C content is less than 0.10%, the steel plate cannot acquire sufficient hardness. On the other hand, when the C content exceeds 0.20%, weldability, low temperature toughness and workability are reduced. Thus, the C content is limited to a value that is within the range of 0.10% to 0.20%. The C content is preferably limited to a value that is within the range of 0.14% to 0.17%.
    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 effectively to the improvement of the strength of the steel plate through reinforcement of solid solution. The Si content is set at 0.05% or
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    10/45 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 1.0%, ductility and toughness 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 1.0%. The Si content is preferably limited to a value that is within the range of 0.2% to 0.5%.
    Mn: 0.1% to 2.0% [0035] Mn is an effective element that has an action to improve hardenability. In order to guarantee such an effect, the Mn content is set at 0.1% or more. On the other hand, when the Mn content exceeds 2.0%, weldability is decreased. 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 1.6%. It is more preferable that the Mn content is limited to a value that is within the range of 0.7% to 1.4%.
    P: 0.020% or less [0036] When the P content in steel is large, the decrease in toughness at low temperature 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%. Thus, the P content is limited to 0.020% or less. Excessive reduction in the P content induces a sharp increase in a refining cost and, therefore, it is desirable to set the P content at 0.005% or more.
    S: 0.005% or less [0037] When the S content in steel is large, S is precipitated as MnS. In high-strength steel, MnS becomes a starting point for fracture occurrence and induces deterioration in toughness. Thus, it is desirable that the S content is as low as possible. In the present invention, the permissible S content is 0.005%. Thus, the S content is limited to
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    0.005% or less. Excessive reduction of the S content induces a sharp increase in a refining cost and, therefore, it is desirable to set the S content at 0.0005% or more.
    Al: 0.005% to 0.100% [0038] Al is an effective 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%, weldability 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%.
    [0039] One or two types of components selected from 0.05% to 2.0% Cr or 0.05% to 1.0% Mo [0040] Both Cr and Mo have an action to suppress corrosive wear, and the steel plate optionally contains one type or two types of Cr and Mo.
    [0041] Cr has an effect of increasing the hardenability, thus making a martensitic phase thinner in order to improve toughness at low temperature. Thus, in the present invention, Cr is an important element. Additionally, in a corrosive wear environment where 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 a inhibitory effect thus giving rise to an effect of improving the resistance to corrosive wear. In order to achieve such an effect, the Cr content is set at 0.05% or more. When the Cr content is less than 0.05%, the steel plate cannot exhibit such an effect of
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    12/45 way enough. 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 0.05% to 2.0%. It is preferable to limit the Cr content to a value that is within the range of 0.07% to 1.20%.
    [0042] Mo has an effect of increasing the hardenability, thus making a martensitic phase finer in order to improve the toughness at low temperature. Thus, in the present invention, Mo is an important element. Additionally, in a corrosive wear environment where 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 the resistance to corrosive wear. In order to achieve this effect, the Mo content is set at 0.05% or more. When the Mo content is less than 0.05%, the steel plate cannot exhibit such an effect sufficiently. On the other hand, when the Mo content exceeds 1.0%, weldability is reduced and a manufacturing cost is sharply increased. Thus, the Mo content is limited to a value that is within the range of 0.05% to 1.0%. It is preferable to limit the Mo content to a value that is within the range of 0.10% to 0.50%.
    [0043] Containing both Cr and Mo, it is expected that the resistance to corrosive wear can be noticeably improved. It is based on the estimate that 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, as Cr and Mo have different pH regions respectively where Cr or Mo can exist as an oxygen acid.
    [0044] In order to improve the resistance to corrosive wear, in the present invention, the steel plate contains Cr and Mo that are inside
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    13/45 of the ranges mentioned above, and the content of steel solute Cr and the content of steel solute Mo can be adjusted to satisfy the following formula (1).
    0.05 <(Crsol + 2.5Mosol) <2.0 ...... (1) [0045] (Crsol: the solute content of Cr in steel (% by mass), Mosol: the solute content of Mo steel (% by mass)).
    [0046] When Cr and Mo form carbides or the like and carbides or the like are precipitated as precipitates, the content of the solute Cr or the content of solute Mo is decreased around the precipitates. Thus, the inhibitory effect mentioned above is reduced so that resistance to corrosive wear is reduced. According to the present invention, the content of steel solute Cr (Crsol) and the content of steel solute Mo (Mosol) are adjusted to meet the above mentioned formula (1). In order to sufficiently guarantee the inhibitory effect mentioned above, in the present invention, it is necessary to set (Crsol + 2.5Mosol) at 0.05 or more. On the other hand, when (Crsol + 2.5Mosol) exceeds 2.0, the inhibitory effect is saturated and, at the same time, a manufacturing cost increases sharply. It is preferable that (Crsol + 2.5Mosol) be set at a value that is within the range of 0.10 to 1.0.
    [0047] The solute content Cr and the solute content Mo can be calculated using the method below. The steel is extracted by electrolysis in an electrolytic solution containing 10% acetylacetone, and an extracted residue obtained (precipitates) is analyzed using an inductively coupled plasma atomic emission spectrophotometry method. The Cr content contained in the extracted residue and the Mo content contained in the extracted residue are respectively determined as the precipitated Cr content and the precipitated Mo content. The Cr solute content and the Mo solute content are obtained by subtracting the determined values from the total Cr content and the total Mo content respectively.
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    14/45 [0048] Additionally, in order to enable the solute content Cr and the solute content Mo to satisfy formula (1), it is necessary to suppress carbide and similar precipitation as much as possible. For this purpose, it is necessary to adjust the heat history or to control the Nb content and the Ti content. In order to be more specific, for example, it is desirable to find a time when the steel is kept in a temperature range (500 ° C to 800 ° C) in which carbide or similar to Cr or Mo precipitates as short as possible or to add Nb or Ti which is more likely to form carbide or similar than Cr and Mo.
    [0049] The components mentioned above are the basic components of steel, according to the present invention. Additionally, steel according to the present invention may optionally 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 consisting of 0.005% to 0 , 2% Sn and 0.005% to 0.2% 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.
    [0050] 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 .
    [0051] All Nb, Ti and V are elements that precipitate as precipitates such as carbonitride and the like, and improve the toughness of steel through refining the structure. In the present invention, when
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    15/45 necessary, steel can contain one or two or more types of components selected from a group consisting of Nb, Ti and V. [0052] Nb is an element that precipitates as a carbonitride and contributes effectively to the improvement of toughness through refining the structure. The Nb content can preferably be set at 0.005% or more to guarantee such an effect. On the other hand, when the Nb content exceeds 0.1%, weldability is decreased. Thus, 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.
    [0053] Ti is an element that precipitates as TiN and contributes to the improvement of toughness through the fixation of solute N. The Ti content is preferably 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 decreased. Thus, 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 most 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.
    [0054] 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 preferably set at 0.005% or more in order to achieve such an effect. On the other hand, when the V content exceeds 0.1%, weldability is decreased. 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%.
    [0055] One or two types of components selected from
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    16/45 a group consisting of 0.005% to 0.2% of Sn and 0.005% to 0.2% of Sb.
    [0056] Both Sn and Sb are elements that improve the resistance to corrosive wear. In the present invention, when necessary, steel may contain one or two types of elements selected from a group consisting of Sn and Sb.
    [0057] 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 preferably set at 0.005% or more to achieve such an effect. On the other hand, when the Sn content exceeds 0.2%, deterioration of ductility and toughness of the steel plate is 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 undesirable elements.
    [0058] 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 cathodic reaction, thereby improving resistance to corrosive wear. The Sb content is preferably set at 0.005% or more to sufficiently achieve such an effect. On the other hand, when the Sb content exceeds 0.2%, the deterioration of toughness of the steel plate is 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%. IS
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    17/45 It is more preferable that the Sb content is set at a value that is within the range of 0.005% to 0.1%.
    [0059] 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.
    [0060] All of Cu, Ni and B are elements that improve temperability. In the present invention, when necessary, steel may contain one or two or more types of elements selected from a group consisting of Cu, Ni and B.
    [0061] Cu is an element that contributes to the improvement of temperability. The Cu content can be preferably 0.03% or more to achieve such an effect. On the other hand, when the Cu content exceeds 1.0%, hot workability is decreased, 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.
    [0062] Ni is an element that contributes to the improvement of temperability and also to the improvement of toughness at low temperature. The Ni content can be preferably 0.03% or more to achieve such an effect. On the other hand, when the Ni content exceeds 2.0%, a manufacturing cost increases. Thus, 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.
    [0063] B is an element that contributes to the improvement of
    Petition 870190039051, of 25/04/2019, p. 21/56
    18/45 hardenability with a small amount contained in steel. The B content can be preferably 0.0003% or more to achieve such an effect. On the other hand, when the B content exceeds 0.0030%, the toughness is decreased. 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, more preferably, within a range of 0.0003% to 0.0015% from a cold crack suppression point of view in a welded part formed by a low heat input weld such as CO2 welding generally used in welding an abrasion resistant steel plate.
    [0064] 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 .
    [0065] 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. In the present invention, when necessary, steel may contain one or two or more types of components selected from a group consisting of REM, Ca and Mg.
    [0066] REM fixes S, thereby suppressing the formation of MnS which causes a decrease in toughness. The REM content can be preferably 0.0005% or more to achieve such an effect. On the other hand, when the REM content exceeds 0.008%, the inclusions content in the steel is increased so that the toughness is reduced in reverse. Thus, 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%.
    [0067] Ca fixed S thus suppressing the formation of MnS which causes a decrease in toughness. Ca content may be preferable
    Petition 870190039051, of 25/04/2019, p. 22/56
    19/45 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 so that the toughness is decreased in reverse. Thus, 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 most preferably set at a value that is within the range of 0.0005% to 0.0030%.
    [0068] Mg fixes S, thereby suppressing the formation of MnS that causes the decrease in toughness. The Mn content can preferably be 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 is increased so that the toughness is reduced in reverse. Thus, 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%.
    [0069] The abrasion-resistant steel plate according to the present invention has the aforementioned composition and, in addition, has a microstructure comprising a martensitic phase in the cooled condition forming a main phase and austenite grains (γ) grain size of 30 μm or less. In this document, a phase that occupies 90% or more in an area ratio is defined as the main phase.
    [0070] Martensitic phase in the cooled condition: 90% or more in the area ratio [0071] When the phase fraction of the martensitic phase in the cooled condition is less than 90% in an area ratio, steel cannot guarantee the desired hardness, and wear resistance is decreased so that the desired wear resistance cannot be guaranteed. Additionally, steel cannot guarantee low toughness
    Petition 870190039051, of 25/04/2019, p. 23/56
    20/45 enough temperature. Additionally, in the case of tempered martensite, Cr and Mo form carbide together with Fe when cementite is formed by quenching and, therefore, Cr sol and Mo solute, which are effective in ensuring corrosion resistance, are decreased. Thus, the martensitic phase is maintained in the martensitic phase in the cooled condition where the martensitic phase is not tempered. An area ratio of the martensitic phase in the cooled condition is preferably set at 95% or more.
    [0072] Previous austenite (γ) grain size: 30 qm or less [0073] Even when the martensitic phase in the cooled condition is guaranteed, the area ratio of 90% or more, when a grain size of previous austenite (γ) grains becomes coarse exceeding 30 qm, low temperature toughness is reduced. As the previous austenite (γ) grain size, 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 .
    [0074] The abrasion-resistant steel plate according to the present invention, which has the aforementioned composition and the structure has a surface hardness of 360 or more in Brinel HBW 10/3000 hardness.
    [0075] Surface hardness: 360 or more in Brinel HBW 10/3000 hardness [0076] When the steel surface hardness is less than 360 in Brinel HBW 10/3000 hardness, the service life of the abrasion-resistant steel plate is makes it short. Brinel hardness is measured according to the stipulation described in JIS Z 2243 (2008).
    [0077] In the following, the preferred method of making the abrasion-resistant steel plate of the present invention is explained.
    Petition 870190039051, of 25/04/2019, p. 24/56
    21/45 [0078] The steel material that has the aforementioned composition is subjected to hot rolling as it is without cooling when the steel material maintains a predetermined temperature or after cooling and reheating, thereby manufacturing a steel plate that has a desired size and a desired shape.
    [0079] The method for making steel material is not particularly limited. It is desirable that the molten steel having the aforementioned composition is 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 is not necessary to mention that a steel material can be manufactured using an ingot casting-roughing method.
    [0080] Reheat temperature: 950 to 1,250 ° C [0081] When the reheat temperature is below 950 ° C, the resistance to deformation becomes excessively high so that a rolling load becomes excessively large in this way. hot rolling 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.
    [0082] The reheated steel material or the 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 to treat it
    Petition 870190039051, of 25/04/2019, p. 25/56
    22/45 direct tempering (DQ), in which the steel plate is cooled immediately after the end of the hot rolling, is applied to the steel plate. It is preferred that a cooling start temperature is set at a temperature not below a transformation point of Ar3. To establish the cooling start temperature equal to or greater than the Ar3 transformation point, it is preferable to set the hot rolling end temperature to a value that is within the range of 800 to 950 ° C, being equal a or greater than the Ar3 transformation point. A cooling cooling rate is not particularly limited as long as the cooling cooling rate is equal to or greater than a cooling rate at which a martensitic phase is formed.
    [0083] A cooling interruption temperature is preferably set at a temperature equal to or below a Ms. point. It is more preferred that the cooling interruption temperature is set at 300 ° C or less to prevent a martensitic phase in the condition cooled to be self-tempered. It is additionally preferred that the cooling interruption temperature is set at 200 ° C or less.
    [0084] After the hot rolling is completed, in place of the direct quench treatment in which a steel plate is immediately cooled, reheat quench treatment (RQ) can be carried out in which the steel plate is cooled by air after the hot rolling is completed afterwards, the steel plate is reheated to a predetermined heating temperature and then the steel plate is cooled. It is desirable that the reheat cooling temperature is set at a value that is within the range of 850 to 950 ° C. A cooling rate of cooling after reheating is not particularly limited as long as the rate of cooling
    Petition 870190039051, of 25/04/2019, p. 26/56
    23/45 cooling cooling after reheating is equal to or greater than a cooling rate at which a martensitic phase is formed. A cool-down temperature is preferably set at a temperature equal to or below a Ms. point. The cool-down temperature is most preferably set at 300 ° C or less to prevent a martensitic phase in the cooled condition from being self-tempered. The cooling interruption temperature is still preferably set at 200 ° C or less.
    EXAMPLE 1 [0085] Hereinafter, the present invention is further explained on the basis of the examples.
    [0086] 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 heated to the reheating temperatures described in Tables 2 and 3 and, subsequently, the steel materials were subjected to hot rolling under conditions described in Table 2 and Table 3, and direct tempering treatment (DQ) was carried out in which the cooling is carried out immediately after the hot lamination is completed (direct cooling). The reheat quenching treatment (RQ) was applied to some steel plates where the steel plates were cooled by air after the hot rolling was completed, the steel plates were reheated to the heating temperatures described in Tables 2, 3 and, subsequently, cooling was performed.
    [0087] The specimens were sampled from the fabricated steel plates, and the specimens were subjected to an observation of the structure, a surface hardness test, an impact test
    Petition 870190039051, of 25/04/2019, p. 27/56
    24/45
    Charpy and a corrosive wear resistance test. The specimens for electrolytic extraction were sampled from the manufactured steel plates, and the specimens were subjected to electrolysis in an electrolytic solution of 10% AA (electrolytic solution of 1% methyl alcohol - tetramethylammonium chloride - 10% acetylacetone), and waste has been extracted. For each of the extracted residues obtained, the Cr content contained in the extracted residue and the Mo content contained in the extracted residue were analyzed using an inductive coupled plasma atomic emission spectrophotometry method, and the content of Cr in the form of precipitates and the Mo content in the form of precipitates were calculated. The content of Cr solute (Crsol) and the solute content Mo (Mosol) were obtained by subtracting the content of Cr in the form of precipitates and the content of Mo in the form of precipitates from the total content of Cr and the total content Mo's respectively.
    [0088] The following test methods have been adopted.
    (1) STRUCTURE OBSERVATION [0089] The specimens for observation of structure were sampled from steel plates manufactured in a position of 1/2 thickness of steel plate plate so that an observation surface becomes a cut perpendicular to the rolling direction. The specimens were polished and attacked by a picric acid to expose grains of γ previous and, subsequently, submitted to observation through an optical microscope (magnification: 400 times). The equivalent circle diameters of the respective 100 grains of previous γ grains were measured, an arithmetic mean was calculated based on the equivalent circle diameters obtained, and the arithmetic mean was established as the previous γ grain size of the steel plate.
    [0090] Thin-film specimens (specimens for observation of structure through a transmission electron microscope) were
    Petition 870190039051, of 25/04/2019, p. 28/56
    25/45 sampled from steel plates manufactured at a 1/2 plate thickness position of the steel plate being parallel to a plate surface. The specimen was ground and polished (mechanical polishing, electrolytic polishing), thus forming a thin film. Next, 20 fields of view for each were observed by a transmission electron microscope (magnification: 20,000 times). A region in which cementite does not precipitate was established as a region of martensitic phase in the cooled condition, and the area of the region was measured. The area of the region of the martensitic phase in the cooled condition was indicated by a ratio (%) in relation to the entire structure, and this ratio was established as a martensitic fraction in the cooled condition (area ratio).
    (2) SURFACE HARDNESS TEST [0091] The specimens for measuring surface hardness were sampled from the manufactured steel plates, and the surface hardness HBW 10/3000 was measured according to JIS Z 2243 (2008). In the hardness measurement, a hard tungsten sphere that has a diameter of 10 mm was used, and a load was set at 3,000 kgf.
    (3) CHARPY IMPACT TEST [0092] V-notched specimens were sampled from steel plates manufactured in a 1/2 thick steel plate plate position away from a steel plate surface in the direction ( direction C) perpendicular to the lamination direction according to the stipulation of JIS Z 2242 (2005), and a Charpy impact test was performed. A test temperature was set at -40 ° C and absorbed energy vE-40 (J) was obtained. The number of specimens was three for each of the steel plates, and an arithmetic average of the three specimens is established as the energy absorbed vE-40 from the steel plate. The steel plate that has the absorbed energy vE-40 of 30 J or more
    Petition 870190039051, of 25/04/2019, p. 29/56
    26/45 was evaluated as the steel plate that has excellent low temperature toughness of base material. For steel plates that have a plate thickness of less than 10 mm, 1/2 t sub-size Charpy specimens were used (t: plate thickness). In the case of 1/2 t sub-size Charpy specimens, the steel plate that has the energy absorbed vE-40 of 15 J or more was evaluated as the steel plate that has excellent tenacity of base material.
    (4) CORROSIVE WEAR RESISTANCE TEST [0093] The wear specimens (size: 10 mm thick, 25 mm wide and 75 mm long) were sampled from steel plates manufactured in a position 1 mm apart of a fabricated steel plate surface. These wear specimens were mounted on a wear tester, and a wear test was performed.
    [0094] The wear specimen was mounted on the wear tester so that the wear specimen was perpendicular to a geometric axis of rotation of a tester's rotor and a surface of 25 mmx75 mm was parallel to the circumferential tangential direction of a circle of rotation, 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 that has an average particle size of 0.65 mm and an aqueous solution of NaCl that was prepared so that the concentration became 15,000 mass in ppm were mixed so that a weight ratio between silica sand and the aqueous NaCl solution becomes 3: 2.
    [0095] 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 when the rotor revolutions became 10,800 times in total. After the test is completed, weights of the respective
    Petition 870190039051, of 25/04/2019, p. 30/56
    27/45 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 the amount of weight reduction of steel stipulated in rolled steel for general structure, tensile strength 400 MPa class SS400 (JIS G3101) (conventional example) as a reference value. When the wear resistance ratio was 1.5 or more, the steel plate was rated as the steel plate that has excellent resistance to corrosive wear.
    [0096] The measured results are shown in Table 4 and Table 5.
    Petition 870190039051, of 25/04/2019, p. 31/56
    TABLE 1
    Steel Number Chemical Composition (% by mass) Transformation pointAr3 (° C) Comments Ç Si Mn P s sol.Al Cr Mo Nb, Ti, V Sn, Sb Cu, Ni, B REM, Ca, Mg THE 0.15 0.36 1.38 0.007 0.0017 0.032 0.11751 within the scope of the present invention B 0.13 0.29 0.42 0.009 0.0026 0.028 1.37 Cu: 0.07, Ni: 0.15806 within the scope of the present invention Ç 0.15 0.33 1.05 0.009 0.0019 0.021 0.40Nb: 0.02, Ti: 0.016B: 0.0015774 within the scope of the present invention D 0.19 0.31 1.15 0.008 0.0026 0.0210.12 750 within the scope of the present invention AND 0.20 0.25 1.64 0.008 0.0018 0.0230.21 Ti: 0.014 REM: 0.0015 700 within the scope of the present invention F 0.12 0.35 0.52 0.007 0.0017 0.0300.56 V: 0.041 Ca: 0.0019 786 within the scope of the present invention G 0.14 0.29 1.12 0.007 0.0026 0.029 0.06 0.07 Ti: 0.014,V: 0.016B: 0.0009 Mg: 0.0011 771 within the scope of the present invention H 0.17 0.31 1.01 0.008 0.0021 0.024 0.41 0.09 763 within the scope of the present invention I 0.16 0.25 0.49 0.011 0.0016 0.027 0.81 0.21 Nb: 0.018B: 0.0025792 within the scope of the present invention J 0.15 0.34 1.21 0.010 0.0023 0.023 0.09 0.14 Nb: 0.02, Ti: 0.014B: 0.0013754 within the scope of the present invention K 0.16 0.32 0.99 0.008 0.0025 0.026 1.01 0.22 Nb: 0.02, Ti: 0.014B: 0.0011748 within the scope of the present invention L 0.15 0.33 0.93 0.009 0.0021 0.028 0.76 0.36 Nb: 0.019,Ti: 0.015, V: 0.045B: 0.0013749 within the scope of the present invention
    28/45
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    TABLE 1 (continued)
    0.15
    0.36
    1.01
    0.008
    0.0022
    0.022
    0.10
    0.25
    Nb: 0.019,
    Ti: 0.013
    B: 0.0012
    761
    0.16
    0.29
    0.95
    0.007
    0.0019
    0.026
    0.31
    Nb: 0.019,
    Ti: 0.014
    Sn: 0.035
    B: 0.0013
    780 within the scope of the present invention
    0.14
    0.21
    1.35
    0.007
    0.0023
    0.025
    0.08
    0.21
    Nb: 0.020,
    Ti: 0.012
    Sn: 0.067
    B: 0.0014
    741 within the scope of the present invention
    0.15
    0.26
    1.09
    0.007
    0.0029
    0.030
    0.80
    0.33
    Nb: 0.017,
    Ti: 0.014
    Sn: 0.045,
    Sb: 0.044
    B: 0.0009
    738 within the scope of the present invention
    0.18
    0.29
    0.87
    0.007
    0.0014
    0.019
    1.10
    0.34
    Nb: 0.029,
    Ti: 0.021, V: 0.034
    Cu: 0.24,
    Ni: 0.31
    Ca: 0.0012
    719 within the scope of the present invention
    29/45
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    TABLE 1 (continued)
    Chemical Composition (% by mass)
    Point of
    Steel Number
    C Si Mn sol.Al Cr
    Mo
    Nb, Ti, V
    Sn,
    Sb
    Cu, Ni, B
    REM, Ca, M g
    transformation of Ar3 (° C)
    Comments
    0.17 0.38
    1.43
    0.008
    0.0016
    0.023 0.02
    Ti: 0.016,
    V: 0.019
    Ca: 0.0013
    743
    0.12 0.37
    1.51
    0.012
    0.0023
    0.030
    0.02
    B: 0.003
    750
    0.16
    0.34
    1.23
    0.0019
    0.021
    0.04
    Ti: 0.014,
    V: 0.025
    Cu: 0.12
    759
    0.14
    0.28
    1.36
    0.007
    0.0019
    0.025
    0.03
    0.02
    Ni: 0.14
    Mg: 0.0021
    748
    0.08
    0.35
    0.98
    0.008
    0.0023
    0.028
    0.19
    0.15
    Underlined values are outside the scope of the present invention.
    Nb: 0.022
    792 outside the scope of the present invention outside the scope of the present invention outside the scope of the present invention outside the scope of the present invention
    30/45
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    TABLE 2
    Steel Plate Number Steel Number Plate Thickness (mm) Treatment Type * Hot rolling Heat treatment Reheat temperature (° C) Rolling End Temperature (° C) Cooling Start Temperature (° C) Cooling Method Cooling interruption temperature (° C) Heating Temperature (° C) Cooling Method Cooling interruption temperature (° C) 1 THE 12 RQ 1,110 860air-cooled870 water-cooled 250 2 THE 19 DQ 1,110 870 840 water-cooled 200 - - - 3 THE 35 DQ 1,110 880 850 water-cooled 230 - - - 4 B 6 RQ 1,120 910 - air-cooled - 880 water-cooled 150 5 B 19 RQ 1,120 930 - air-cooled - 900 water-cooled 150 6 B 32 DQ 1,120 870 800 water-cooled 150 - - - 7 Ç 6 RQ 1,120 850 - air-cooled - 950 water-cooled 200 8 Ç 12 RQ 1,120 860 - air-cooled - 870 water-cooled 200 9 Ç 19 DQ 1,120 890 830 water-cooled 150 - - - 10 D 19 DQ 1,050 840 810 water-cooled 150 - - - 11 D 25 DQ 1,050 850 800 water-cooled 150 - - - 12 D 35 DQ 1,050 880 820 water-cooled 130 - - - 13 AND 6 RQ 1,120 840 - air-cooled - 930 water-cooled 150 14 AND 12 RQ 1,120 870 - air-cooled - 900 water-cooled 150
    31/45
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    TABLE 2 (continued)
    DQ
    1,120
    890
    830
    RQ
    1,120
    890 water-cooled air-cooled
    150
    900 water-cooled
    150
    DQ
    1,120
    870
    850
    DQ
    1,120
    890
    840
    DQ
    1,150
    920
    880
    RQ
    1,150
    930 water cooled water cooled water cooled air cooled
    150
    170
    160
    900 water-cooled
    150
    32/45
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    TABLE 2 (continued)
    Steel Plate Number Steel Number Plate Thickness (mm) Type of Treatment * Hot rolling Heat treatment Reheat temperature (° C) Rolling End Temperature (° C) Cooling Start Temperature (° C) Cooling Method Cooling interruption temperature (° C) Heating Temperature (° C) Cooling Method Cooling interruption temperature (° C) 21 G 35 DQ 1,150 910 870 water-cooled 200 - - - 22 H 6 RQ 1,120 910 - air-cooled - 880 water-cooled 150 23 H 19 RQ 1,120 930 - air-cooled - 900 water-cooled 150 24 H 32 RQ 1,120 870 - air-cooled - 900 water-cooled 150 25 I 12 RQ 1,120 900 - air-cooled - 900 water-cooled 170 26 I 19 RQ 1,120 920 - air-cooled - 910 water-cooled 170 27 I 25 DQ 1,120 880 830 water-cooled 210 - - - 28 I 12 DQ 1,170 900 860 water-cooled 210 - - - 29 J 25 DQ 1,170 920 880 water-cooled 220 - - - 30 J 35 RQ 1,170 880 - air-cooled - 900 water-cooled 160 37 K 6 RQ 1,070 900 - air-cooled - 900 water-cooled 170
    33/45
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    TABLE 2 (continued)
    K 19
    RQ 1.170
    920
    K
    RQ 1.120
    860
    L
    RQ
    1,120
    880
    L 19
    RQ
    1,120
    900
    L 25
    RQ
    1,120
    890 air-cooled air-cooled air cooled by air cooled
    900
    900
    870
    920
    900
    Underlined values are outside the scope of the present invention.
    * DQ: direct cooling, RQ: water-cooled water-cooled reheat cooling water-cooled water-cooled
    170
    170
    170
    170
    170
    34/45
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    TABLE 3
    Steel Plate Number Steel Number Plate Thickness (mm) Treatment Type * Hot rolling Heat treatment Reheat temperature (° C) Rolling End Temperature (° C) Cooling Start Temperature (° C) Cooling Method Cooling interruption temperature (° C) Heating Temperature (° C) Cooling Method Cooling interruption temperature (° C) 43 M 12 RQ 1,120 900 - air-cooled - 910 water-cooled 170 44 M 19 DQ 1,120 870 840 water-cooled 220 - - - 45 M 32 DQ 1,120 890 830 water-cooled 220 - - - 46 N 12 RQ 1,120 900 - air-cooled - 900 water-cooled 150 47 N 25 RQ 1,120 920 - air-cooled - 870 water-cooled 150 48 N 32 RQ 1,120 900 - air-cooled - 880 water-cooled 150 49 O 6 RQ 1,070 880 - air-cooled - 920 water-cooled 150 50 O 12 RQ 1,070 900 - air-cooled - 910 water-cooled 150 51 O 19 RQ 1,070 920 - air-cooled - 900 water-cooled 150 52 P 6 RQ 1,120 920 - air-cooled - 880 water-cooled 150 53 P 25 RQ 1,120 920 - air-cooled - 900 water-cooled 150
    35/45
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    TABLE 3 (continued)
    54 P 32 RQ 1,120 860 - air-cooled - 910 water-cooled 150 55 Q 12 RQ 1,080 900 - air-cooled - 910 water-cooled 150 56 Q 19 DQ 1,080 880 840 water-cooled 150 - - - 57 Q 25 DQ 1,080 860 820 water-cooled 150 - - - 58 R 6 RQ 1,120 850 - air-cooled - 880 water-cooled 310 59 R 19 DQ 1,120 870 830 water-cooled 320 - - - 60 R 35 RQ 1,120 900 - air-cooled - 850 water-cooled 310 61 s 6 DQ 1,150 880 840 water-cooled 310 - - - 62 s 19 DQ 1,150 840 820 water-cooled 310 - - -
    36/45
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    TABLE 3 (continued)
    Steel Plate Number Steel Number Plate Thickness (mm) Type of Treatment * Hot rolling Heat treatment Reheat temperature (° C) Rolling End Temperature (° C) Cooling Start Temperature (° C) Cooling Method Cooling interruption temperature (° C) Heating Temperature (° C) Cooling Method Cooling interruption temperature (° C) 63 s 35 DQ 1,150 820 810 water-cooled 310 - - - 64 T 19 RQ 1,130 930 - air-cooled - 900 water-cooled 310 65 T 25 DQ 1,130 920 890 water-cooled 310 - - - 66 T 35 DQ 1,130 850 830 water-cooled 310 - - - 67 U 12 RQ 1,200 860 - air-cooled - 900 water-cooled 320 68 U 25 RQ 1,200 890 - air-cooled - 900 water-cooled 310 69 U 35 DQ 1,200 880 840 water-cooled 310 - - - 70 V 12 RQ 1,180 840 - air-cooled - 900 water-cooled 210 71 V 19 RQ 1,180 930 - air-cooled - 930 water-cooled 210 72 V 30 DQ 1,180 900 850 water-cooled 210 - - -
    Underlined values are outside the scope of the present invention.
    * DQ: direct cooling, RQ: reheating cooling
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    TABLE 4
    Steel Plate Number Steel Number Solute Content Structure Surface hardness Low temperature toughness Corrosive Wear Resistance Comments Crsol + 2.5Mosol(% in large scale) Grain Size of previous Austenite Grain (one) Martensite fraction (% area) HBW 10/3000 vE-40(J) Wear resistance ratio (Reference: 1.0 (conventional example)) 1 THE 0.07 26 93 405 40 1.59 example of the present invention 2 THE 0.08 21 91 413 36 1.54 example of the present invention 3 THE 0.07 19 90 418 33 1.51 example of the present invention 4 B 1.21 19 95 382 60 2.23 example of the present invention 5 B 1.18 21 93 386 83 2.28 example of the present invention 6 B 1.20 23 91 390 80 2.27 example of the present invention 7 Ç 0.36 20 94 427 47 1.67 example of the present invention 8 Ç 0.35 22 93 430 72 1.73 example of the present invention 9 Ç 0.35 24 91 431 60 1.66 example of the present invention 10 D 0.23 27 93 469 50 1.57 example of the present invention
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    Petition 870190039051, of 25/04/2019, p. 42/56
    TABLE 4 (continued)
    11 D 0.25 28 92 472 47 1.53 example of the present invention 12 D 0.26 29 90 474 42 1.56 example of the present invention 13 AND 0.44 23 96 479 40 1.77 example of the present invention 14 AND 0.45 21 94 482 61 1.80 example of the present invention 15 AND 0.44 24 92 486 57 1.75 example of the present invention 16 F 1.03 19 94 365 75 2.12 example of the present invention 17 F 1.05 21 93 364 72 2.18 example of the present invention 18 F 1.04 24 91 362 69 2.14 example of the present invention 19 G 0.21 22 93 406 65 1.61 example of the present invention 20 G 0.22 24 91 397 70 1.66 example of the present invention
    39/45
    Petition 870190039051, of 25/04/2019, p. 43/56
    TABLE 4 (continued)
    Steel Plate Number Steel Number Solute Content Structure Surface hardness Low temperature toughness Corrosive Wear Resistance Comments Crsol + 2.5Mosol(% in large scale) Grain Size of previous Austenite Grain (one) Martensite fraction (% area) HBW 10/3000 vE-40(J) Wear resistance ratio (Reference: 1.0 (conventional example)) 21 G 0.22 23 91 401 66 1.66 example of the present invention 22 H 1.21 23 95 433 40 2.22 example of the present invention 23 H 1.18 25 93 436 55 2.24 example of the present invention 24 H 1.20 24 91 430 59 2.21 example of the present invention 25 I 1.13 10 96 435 101 2.29 example of the present invention 26 I 1.14 14 94 438 97 2.22 example of the present invention 27 I 1.12 13 93 440 93 2.20 example of the present invention 28 I 0.29 17 94 410 85 2.00 example of the present invention 29 J 0.30 18 95 413 80 2.01 example of the present invention 30 J 0.29 14 91 406 84 2.02 example of the present invention
    40/45
    Petition 870190039051, of 25/04/2019, p. 44/56
    TABLE 4 (continued)
    1.33
    436
    2.44
    K 1.35
    430
    100
    2.47
    1.31
    433
    105
    2.45
    1.23
    420
    2.27 example of the present invention example of the present invention example of the present invention example of the present invention
    L 1.25
    419
    103
    2.28 example of the present invention
    L 1.26
    Underlined values are outside the scope of the present invention.
    416
    104
    2.22 example of the present invention
    41/45
    Petition 870190039051, of 25/04/2019, p. 45/56
    TABLE 5
    Steel Plate Number Steel Number Solute Content Structure Surface hardness Low temperature toughness Corrosive Wear Resistance Comments Crsol + 2.5Mosol(% inpasta) Grain size of previous Austenite Grain (pm) Martensite fraction (% area) HBW10/3000 vE-40(J) Wear resistance ratio (Reference: 1.0 (conventional example)) 43 M 0.36 13 95 415 83 1.97 example of the present invention 44 M 0.35 17 93 413 79 1.99 example of the present invention 45 M 0.37 19 91 409 77 1.95 example of the present invention 46 N 0.22 16 94 440 81 2.09 example of the present invention 47 N 0.22 13 92 432 89 2.03 example of the present invention 48 N 0.21 15 91 425 83 2.00 example of the present invention 49 O 0.35 15 95 405 55 2.10 example of the present invention 50 O 0.36 14 94 409 86 2.06 example of the present invention 51 O 0.35 13 93 403 92 2.10 example of the present invention
    TABLE 5 (continued)
    42/45
    Petition 870190039051, of 25/04/2019, p. 46/56
    52 P 1.21 15 98 425 55 2.40 example of the present invention 53 P 1.19 14 96 419 81 2.42 example of the present invention 54 P 1.18 15 96 423 80 2.42 example of the present invention 55 Q 1.51 9 99 462 110 2.44 example of the present invention 56 Q 1.50 7 98 466 99 2.47 example of the present invention 57 Q 1.50 6 97 460 103 2.42 example of the present invention 58 R 0.01 36 91 436 11 0.78 comparative example 59 R 0.01 34 93 441 24 0.73 comparative example 60 R 0.01 38 90 433 14 0.76 comparative example 61 s 0.01 35 88 355 13 0.80 comparative example 62 s 0.02 33 87 352 25 0.70 comparative example
    43/45
    Petition 870190039051, of 25/04/2019, p. 47/56
    TABLE 5 (continued)
    Steel Plate Number Steel Number Solute Content Structure Surface hardness Low temperature toughness Corrosive Wear Resistance Comments Crsol + 2.5Mosol(% in large scale) Previous Austenite Grain Size (pm) Martensite fraction (% area) HBW10/3000 vE-40(J) Wear resistance ratio (Reference: 1.0 (conventional example)) 63 s 0.01 31 86 348 27 0.74 comparative example 64 T 0.04 29 90 435 25 0.92 comparative example 65 T 0.03 28 88 441 21 0.95 comparative example 66 T 0.03 29 88 440 23 1.00 comparative example 6Z U 0.04 31 89 401 25 1.14 comparative example 68 U 0.04 32 87 396 22 1.07 comparative example 69 U 0.04 32 86 394 20 1.11 comparative example Z0 V 0.29 24 91 290 60 0.64 comparative example Z1 V 0.31 26 90 295 55 0.65 comparative example Z2 V 0.30 23 92 299 53 0.66 comparative example
    Underlined values are outside the scope of the present invention.
    44/45
    Petition 870190039051, of 25/04/2019, p. 48/56
    45/45 [0097] All examples of the present invention exhibit surface hardness of 360 or more in HBW 10/3000, excellent low temperature toughness of vE-40 of 30 J or more (15 J or more in a case of the specimen 1/2 t), and excellent corrosive wear resistance of the wear resistance ratio of 1.5 or more. 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 (5)
    [1]
    1. Abrasion-resistant steel plate having excellent low temperature toughness and excellent resistance to corrosive wear, characterized by the fact that it has a composition containing, in mass%:
    0.10% to 0.20% 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, one or two types of components selected from a group consisting of:
    0.05% to 2.0% Cr, and
    0.05% to 1.0% Mo, and
    Remaining Fe and unavoidable impurities as a balance, in which the solute content of Cr in steel and the solute content of Mo in steel satisfy the following formula (1), the steel plate having a structure in which a martensitic phase in the condition of cooled forms a main phase and a grain size of previous austenite grains is 30 gm or less, and the surface hardness of the steel plate is 360 or more in HBW10 / 3000 Brinel hardness.
    0.05 <(Crsol + 2.5Mosol) <2.0 ... (1) where:
    Crsol: the content of Cr solute in steel (% by mass), and
    Mosol: the content of solute Mo in steel (% by mass)
    [2]
    2. Abrasion-resistant steel plate according to claim 1, characterized by the fact that the steel composition additionally contains, in mass%, one or two or more types of
    Petition 870190039051, of 25/04/2019, p. 50/56
    2/2 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% of V.
    [3]
    3. Abrasion-resistant steel plate according to claim 1 or 2, characterized by the fact that 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% Sb.
    [4]
    4. Abrasion-resistant steel plate according to any one of claims 1 to 3, characterized in that the steel composition additionally contains in% by weight, one or two or more types of components selected from a group that consists 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 in that the steel composition additionally contains, in mass%, one or two or more types of components selected from a group consisting of:
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    法律状态:
    2018-11-21| B06F| Objections, documents and/or translations needed after an examination request according art. 34 industrial property law|
    2019-02-05| B06A| Notification to applicant to reply to the report for non-patentability or inadequacy of the application according art. 36 industrial patent law|
    2019-06-11| B09A| Decision: intention to grant|
    2019-08-13| B16A| Patent or certificate of addition of invention granted|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
    JP2012205305|2012-09-19|
    PCT/JP2013/005434|WO2014045553A1|2012-09-19|2013-09-13|Wear-resistant steel plate having excellent low-temperature toughness and corrosion wear resistance|
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