high-strength galvanized steel sheet

专利摘要:
agglomerate containing unburned carbon for blast furnaces and its production process the present invention relates to cold-bonded composite carbon agglomerates have a carbon content (tc) in the range of 18 to 25% by mass, and a ca0 ratio / si02 between a dog content (mass%) and a si02 content (mass%) in a range of 1.0 to 2.0. the process for making cold-bonded composite carbon agglomerates includes: forming a molded body by mixing and kneading raw materials containing iron, raw materials containing carbon, and a binder and molding a kneaded substance to obtain the shaped body; and obtaining cold-bonded carbon composite agglomerates through subsequent curing of the molded body, in which both one and both conditions of combining an iron ore brand and an amount of combination of binder are adjusted in the formation of the molded body that a carbon content (tc) becomes in a range of 18 to 25% by mass and a dog / sioz ratio between a dog content (% by mass) and a sioz content (% by mass) as mineral constituents of denim becomes a range of 1, o to 2.0 in the cold-bonded carbon composite agglomerates.
公开号:BR112012004303B1
申请号:R112012004303
申请日:2010-08-31
公开日:2020-05-05
发明作者:Miyasaka Akihiro；Honda Kazuhiko；Azuma Masafumi；Fujita Nobuhiro；Suzuki Noriyuki；Nonaka Toshiki；Morimoto Yasuhide
申请人:Nippon Steel & Sumitomo Metal Corp；Nippon Steel Corp；
IPC主号:

专利说明:

Invention Patent Descriptive Report for HIGH-RESISTANCE GALVANIZED STEEL SHEETS.
Technical Field [001] The present invention relates to a high strength galvanized and annealed galvanized steel sheet and a method of producing it.
[002] Priority is claimed over the Patent Application
Japanese No. 2009-200467, filed on August 31, 2009, Japanese Patent Application No. 2009-217578, filed on September 18, 2009, and Japanese Patent Application No. 2009-216986, filed on 18 September 2009, whose contents are incorporated here as a reference.
Background of the Technique [003] A typical example of a coated sheet having favorable corrosion resistance is a galvanized and annealed steel sheet. The galvanized and annealed steel sheet is generally produced by degreasing a steel sheet, preheating the steel sheet in a non-oxidizing oven or direct heating furnace, by performing reduction annealing in a reduction furnace to clean the surface and ensure the quality of the material, immerse the steel sheet in a galvanizing bath, control the amount of molten zinc adhered to, and perform the connection. Since the steel sheet has excellent corrosion resistance, adhesion capacity, and the like, the steel sheet is widely used mainly for automobiles, building materials, and the like.
[004] Particularly, in recent years, to guarantee both the function to protect passengers in the event of a collision and to reduce weight to improve mileage in the automobile field, there was a demand for an increase in the resistance of
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2/71 a coated steel sheet. However, generally an increase in strength results in degradation of the forming capacity, and thus there has been a demand to establish a method for increasing the strength while the forming capacity is maintained.
[005] Examples of the method for increasing the strength while the forming capacity is maintained include methods as described in Patent Documents 1 and 2. These methods are for increasing the resistance and obtaining a favorable forming capacity at the same time by dispersing the austenite in steel and using the fact that residual austenite causes stress induction and strain induction during a process. In the steel plate as described in Patent Documents 1 and 2, C, Si and Mn are used as basic bonding elements, annealing is carried out in a region of two phases of ferrite (a) + austenite (γ), and then a heat treatment is carried out in a temperature region of approximately 300 ° C to 450 ° C, thus using a bainite transformation and obtaining residual austenite even at room temperature. However, since carbides, such as cementite, tend to precipitate during heat treatment from 300 ° C to 450 ° C, and austenite and decomposed, it is necessary to add Si or Al.
[006] However, since Si and Al are more likely to be oxidized than Fe, it is likely that oxides containing Si or Al will be formed on the surface of the steel plate above. These oxides have wetting properties with molten Zn, and thus, in steels containing Si or Al, there is a problem that uncoated portions are liable to be formed. In addition, the oxides above delay the bonding reaction between Zn and Fe. Therefore, in steel sheets containing Si or Al, a long bonding treatment with a high
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3/71 temperature is required compared to mild steel sheets, productivity degradation is caused, austenite is decomposed in a bainite structure including perlite and carbides by long bonding treatment at high temperature, and an excellent forming capacity cannot be obtained.
[007] Patent Document 3 describes a method for solving the above problems. This method is to improve the wetting properties of steel sheets and molten Zn to accelerate the bonding reaction by adding an appropriate concentration of Al to molten Zn.
[008] This method makes it possible to suppress the spread of fatigue fractures that propagate through soft ferrite by the structural reinforcement that reinforces soft ferrite using a hard structure, such as hard martensite or residual austenite, and so this method contributes to improving durability from fatigue to a certain fraction of hard phases. However, since the fatigue fracture spreads through soft structures, there is a limit to increasing the fatigue limit simply by increasing the fraction of hard structures. As a result, when the fraction of hard structures reaches a certain extent or more, the strength of the steel sheet is increased, but the fatigue limit is not increased. Therefore, it was difficult to achieve both an increase in strength and durability of fatigue to a high level (for example, refer to Non-Patent Document 1).
[009] Meanwhile, since steel sheets used for automobiles or construction materials are thin in thickness, there are cases where, when the fatigue fracture is formed, the thickness of the sheet is immediately penetrated and fractured. Because of this, the suppression of the formation of fatigue fractures is particularly important;
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4/71 [0010] Common techniques for improving fatigue durability include a method of using precipitation reinforcement (for example referring to Patent Document 4). However, to use precipitation reinforcement, it is necessary to heat the steel sheet to a high temperature sufficient to melt the precipitates (for example, Nb or Ti carbonitrides) and then cool the steel sheet, so this technique can be applied to hot-rolled steel sheets, but it is difficult to apply this technique to cold-rolled steel sheets.
[0011] In addition, Patent Document 5 describes a technique that isolates and disperses a soft phase (ferrite) in a second hard phase, and controls the thickness of the hard phase so that it is greater than the value specified by the grain diameter of the soft phase, thus improving fatigue durability. However, this technique is to suppress the spread of fractures formed on the surface of the steel sheet, and it is not to suppress the formation of fractures on the surface, and therefore it is difficult to sufficiently improve the fatigue life of the steel sheet using this technique. .
[0012] In addition, Patent Document 6 describes a technique that controls the oxide depths of the grain edges at the interface between a coated layer and a steel sheet to 0.5 μm or less, thereby improving fatigue life. The reason the fatigue life is improved is considered to be because the decrease in the depths of the oxides of the grain edges suppresses the concentration of stress at the interface between the coated layer and the steel plate. However, even with this technique, it was difficult to sufficiently suppress the formation of fractures on the surface.
[0013] In addition, the addition of Si to steel is performed as an inexpensive method of reinforcing a high-strength steel plate. However, when the amount of Si in the steel sheet exceeds 0.3%
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5/71 by mass, there is a problem due to the fact that the wetting properties are significantly degraded in the Sendzimir method in which a coating bath containing common Al is used, parts of the surface are not coated, and therefore the appearance quality is deteriorated . It is reported that the above phenomenon is because Si oxides are concentrated on the surface of the steel sheet during reduction annealing, and the wetting properties of Si oxides in relation to molten Zn are deteriorated.
[0014] As measures to solve the above problems, the
Patent Document 7 describes a method in which heating is performed in an atmosphere having an air ratio of 0.9 to 1.2 in order to generate Fe oxides, the thickness of the oxides is controlled to 500 Å or less in one reduction zone in an atmosphere including H2, and then the coating is carried out in a bath to which Mn and Al are added. However, in the current production lines, various types of steel sheets including a variety of added elements are carefully directed, which makes it very difficult to control the thickness of the oxides. In addition, Patent Documents 8, 9, and the like describe methods in which the specific coating is performed in order to improve the coating properties like other measures for suppression, but these methods require the installation of new coating equipment for the galvanizing line after the annealing furnace, or requires a coating treatment that is carried out before the electrical coating line, which significantly increases costs.
[0015] Steel sheets having a tensile strength of, commonly, 780 MPa or more e. recently, 980 MPa or more are used as high-strength steel sheets for
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6/71 car reinforcement. High-strength steel sheet is generally formed by a process that is used mainly for bending. It is known that a high strength steel sheet having a high concentration of C increases the hardness of the steel sheet itself, and the average hardness of the steel sheet surface layer, which is measured by the nano-recess method, exceeds 3 , 5 GPa.
[0016] Here, the nano-indentation method refers to one of the methods for evaluating the mechanical properties of thin films. In this method, a small needle is pressed to the measurement target of a thin film under a certain load, the depth of ingress of the needle is measured with a precision of nanometer (nm), and the values of properties, such as hardness or elasticity, thin film are computed.
[0017] A problem in a case where a high strength steel sheet having a high concentration of C is used is hydrogen embrittlement. Hydrogen embrittlement that is caused by atomic hydrogen that has intruded on the grain edge and is similar under an internal tension-resistant tension, such as residual stress. Hydrogen embrittlement can be suppressed by a method in which the hydrogen concentration in the steel is decreased by performing a dehydrogenation treatment after the steel sheet is processed in a member, but the number of steps in production steps is increased and costs are increased.
[0018] In addition, when the surface layer of a high-strength steel sheet is hard, the fracture is likely to occur in the surface layer of the steel sheet during the folding process, the fracture develops during use, and the steel plate is broken in the direction of the thickness of the plate. This degradation of the folding properties causes a significant problem. O
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7/71
Patent Document 4 describes a method in which an isothermal treatment is performed during the annealing step to improve the bending properties, but 3 minutes or more of the isothermal treatment is essential, and this method performed using continuous coating equipment causes significant degradation in productivity.
[0019] In Patent Documents 11 and 12, the structure or concentration of C in the ferrite portion is controlled to improve the coating properties. These documents focus on the surface properties of the ferrite while the coating is carried out. However, these documents do not sufficiently describe the analysis, which is carried out after coating, of the properties of the ferrite portion that adheres directly to the interface with the plate. In the method of Patent Document 12, it is difficult to measure the concentration of C just below the interface, particularly at a depth of 1 qm or less.
List of Citations
Patent Documents [0020] [Patent Document 1] Unexamined Japanese Patent Application, First Publication No. H05-70886 [0021] [Patent Document 2] Unexamined Japanese Patent Application, First Publication No. H05-195143 [ 0022] [Patent Document 3] Unexamined Japanese Patent Application, First Publication No. 2003-105516 [0023] [Patent Document 4] Unexamined Japanese Patent Application, First Publication No. 2006-57120 [0024] [Document Patent 5] Unexamined Japanese Patent Application, First Publication No. 2005-194586 [0025] [Patent Document 6] Unexamined Japanese Patent Application, First Publication No. 2003-171752
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8/71 [0026] [Patent Document 7] Unexamined Japanese Patent Application, First Publication No. H04-276057 [0027] [Patent Document 8] Unexamined Japanese Patent Application, First Publication No. H03-28359 [ 0028] [Patent Document 9] Unexamined Japanese Patent Application, First Publication No. H03-64437 [0029] [Patent Document 10] Unexamined Japanese Patent Application, First Publication No. 2006-9057 [0030] [Document Patent 11] Unexamined Japanese Patent Application, First Publication No. 2002-088459 [0031] [Patent Document 12] Unexamined Japanese Patent Application, First Publication No. 2003-073772
Non-Patent Documents [0032] [Non-Patent Document 1] The preprint of the 40 ^th academic conference by The Japan Institute of Metals, written by Yokomaku Toshinori and three other authors, 1991, pg. 16
Description of the Invention
Technical Problem [0033] To improve the fatigue life of a steel sheet, it is necessary to suppress the formation of fractures on the surface, but it was difficult to suppress the formation of fractures on the surface in the relative technique. The present invention has been made in consideration of such a circumstance, and an objective of the present invention is to provide a high-strength, annealed, galvanized steel sheet that can stably produce favorable fatigue durability.
Solution to the Problem [0034] To solve the problem above, aspects of the present invention are as follows:
[0035] A first aspect of the present invention is a galvanized steel sheet having a tensile strength of 770 MPa or more
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9/71 including a portion of the steel sheet containing, in% by mass, C: 0.05% to 0.50%, Si: 0.005% to 2.5%, Mn: 0.01% to 3.0% , Al: 0% to 0.5%, Ni: 0% to 2.0%, Cu: 0% to 2.0%, Cr: 0% to 2.0%, Mo: 0% to 2.0% , B: 0% to 0.002%, Ti: 0% to 0.1%, Nb: 0% to 0.1%, V: 0% to 0.1%, REM: 0% to 0.1%, and Ca: 0% to 0.1% and a remainder of Fe and the inevitable impurities, in which P, S and N are limited to 0.03% or less, 0.02% or less, and 0.0060% or less respectively, and a coated layer formed on the surface of the sheet steel portion, in which the coated layer is a galvanized coated layer or a galvanized and annealed coated layer, the galvanized coated layer containing Al: 0.01% to 1.5% and one or more elements selected from Pb, Sb, Si, Sn, Mg, Mn, Ni, Cr, Co, Ca, Cu, Li, Ti, Be, Bi, and REM in total from 0% to 3.5% with remainder being Zn and the inevitable impurities, and the galvanized and annealed coated layer containing Fe: 5% to 15%, Al: 0.01% to 1% and one or more elements selected from Pb, Sb, Si, Sn, Mg, Mn, Ni, Cr, Co, Ca, Cu, Li, Ti, Be, Bi, and REM in a total of 0% to 3.5% with the remainder being Zn and the inevitable impurities, the steel plate portion has a soft layer that adheres directly to the interface with the coated layer and an inner layer that is different from the soft layer, the thickness D of the soft layer is 0.001% to 5% of the thickness t of the steel plate portion, and, when the hardness of the layer soft measured by the nano-indentation method is indicated by H1, and the representative hardness of the steel plate portion measured by the nano-indentation method is indicated by Ha in a cross section extending longitudinally to the direction of the thickness of the steel plate portion, H1 is 5% to 75% of Ha.
[0036] N galvanized steel sheet according to item (1) above, when an oxide including one or two elements between Si and Mn is present in the surface layer of the steel sheet within a
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10/71 depth d or less from the plate / ferrite interface, the depth d at which the oxide is present and D can satisfy d / 4 <D <2d.
[0037] In the galvanized steel sheet as per item (1) above, the steel sheet portion may also contain more than 0.10% to 0.50% C.
[0038] In the galvanized steel sheet as per item (1) above, the C concentration in the soft layer can be 10% to less than 30% of the C concentration of the entire steel sheet portion.
[0039] A second aspect of the present invention is a method of producing the galvanized steel sheet as per item (1) above, in which the conditions for annealing before coating on a continuous galvanizing line for the steel sheet portion are: the peak temperature of the plate is controlled to 650 ° C to 900 ° C; the annealing atmosphere at the peak plate temperature is controlled to contain, in% by volume, 1% to 10% hydrogen and the rest composed of nitrogen and the inevitable impurities; and, in addition, the dew point is controlled to be greater than 0 ° C to 50 ° C.
[0040] A third aspect of the present invention is a method for producing the galvanized steel sheet according to item (1) above having a process in which a direct current magnetic field that crosses the thickness of a plate is applied in order to form a zone of electric current field during continuous casting, and an upper tank that forms the upper area of the plate after the casting and a lower tank that forms the lower area are separated, and a process in which the steel material composed of Fe or an alloy containing Fe is supplied to the upper tank.
Advantageous Effects of the Invention
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11/71 [0041] Galvanized steel sheet and galvanized and annealed steel sheet as an aspect of the present invention have excellent fatigue life and resistance to hydrogen embrittlement. In addition, since the fracture does not occur in the surface layer of the coated steel sheet even when the steel sheet is subjected to a bending process, the bending properties are excellent.
[0042] In addition, according to the method according to one aspect of the present invention, it becomes possible to produce a coated steel sheet having excellent fatigue life, resistance to hydrogen embrittlement, and bending properties without degrading productivity.
Brief Description of the Drawings [0043] Figure 1 is a microscopic photograph showing the result of caustication of the typical steel sheet cross section and observing it using an optical microscope.
Description of Modalities [0044] Any of the techniques mentioned above does not consider improvement in the fatigue durability of a coated steel sheet. Fatigue durability is a characteristic of deformation in a case where sufficiently low stress is added repeatedly in relation to tensile strength, and is an indispensable characteristic for structural members that receive repetitive stress, such as automobiles, construction machinery, and building materials. When the steel sheet receives repetitive stress, fine deformation occurs on the steel sheet even when the stress intensity is less than the yield limit, and the accumulation of deformation results in fracture of the steel sheet. This fracture is caused by the fracture that is formed on the surface and propagates in the steel plate. From that fact, it becomes
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12/71 important to suppress the formation of fatigue fracture or suppress the spread of the fracture to improve fatigue durability.
[0045] Particularly, in a case where application to automotive members is taken into account, there is a concern that even fine fractures can act as a starting point for fractures in the event of a vehicle body collision. In this case, since there is a concern that collision stability may not be achieved, it is considered important to suppress the fine fracture to improve the collision characteristics. Therefore, it is particularly important to suppress the formation of fractures to improve the durability of fatigue.
[0046] To suppress the formation of fractures, the characteristics of the coated steel plate, particularly in a portion immediately below the plate interface (a portion that adheres directly to the plate) are important. The portion of the steel plate immediately below the interface, particularly in a range of 1 pm or less from the interface of the plate, sometimes has a different hardness than that of the entire steel plate due to a plurality of causes, such as concentration of increased C compared to the entire steel plate, accumulation of oxides, and formation of a different composition of the steel structure from inside the steel plate. Therefore, it has been found that it is difficult to obtain a stable fatigue life of a coated steel sheet if the production method and quality are not controlled based on an accurate measurement of the hardness of the steel sheet immediately below the sheet interface.
[0047] In the relative technique, when the investigation was performed on a portion of steel below the plate interface, for example, a method was used in which the steel plate is removed using a solution containing an inhibitor, the coating is dissolved to a
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13/71 depth of approximately 5 gm, and the average concentration of carbon and the like in the steel plate are measured. However, in the measurement results by the present inventors, there have been cases in which a stable correlation between the measurement results and the fatigue life was not particularly obtained in high-strength steel sheets having a tensile strength of 770 MPa or more. As a result of further investigation, it has been found that the characteristics of the steel sheet in a portion of a depth of 1 gm or less from the interface are surely correlated with fatigue life. In a measurement according to the relative technique, the measurement range of a portion of a depth of 5 gm or less is very wide, and therefore the characteristics of the steel sheet immediately below the interface cannot be sufficiently investigated, which is considered to be the cause of the poor correlation.
[0048] In addition, as a result of complete repetitive studies on improving the fatigue life of a high strength galvanized and annealed steel sheet, the inventors found that fatigue life can be improved without degrading the forming ability by formation of a microstructure, in which the ferrite area ratio is 95% or more, at the interface between the high-strength steel sheet and the galvanized and annealed coated layer with an average thickness of 0.01 gm to 10 gm. In particular, as long as the ferrite area ratio is adequately controlled immediately below the interface, that is, at a depth of 1 gm or less, the fatigue life can be improved steadily.
[0049] In addition, the inventors found that it is possible to reduce only the hardness of a layer close to the interface, which is the surface portion of the steel plate (the vicinity of the interface of the
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14/71 plate) that does not affect the strength of the steel plate, adjusting the steel components and the processing steps. It has been found that this method can improve the ductility of the layer close to the surface, suppress the occurrence of fracture, and also improve resistance to hydrogen embrittlement. In addition, it has been found that the generation of Si and Mn oxides in the vicinity of the steel sheet surface layer (in the vicinity of the layer close to the interface) can improve resistance to hydrogen embrittlement since the oxides suppress the spread of fractures even when the fracture occurs, and, in addition, the formation of oxides within the steel plate can guarantee favorable coating properties.
(First embodiment) [0050] Hereinafter, a first embodiment of the present invention will be described in detail.
[0051] Initially, the reasons why the steel sheet components are limited will be described. In addition,% in the present invention refers to% by mass unless otherwise specified.
(Steel plate components) [0052] C is an essential element in a case in which an attempt is made to increase the strength of the steel plate through the structural reinforcement that is achieved by residual martensite or austenite. The reason why the amount of C is adjusted to 0.05% or more is that when the amount of C is less than 0.05%, cementite or perlite is likely to be generated in a galvanizing line in which it is difficult to cool the steel sheet from the annealing temperature using mist or water jets as a cooling medium, and it is difficult to guarantee the necessary tensile strength. In order to stably achieve a high resistance of 770 MPa or more, the amount of C is preferably
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15/71 adjusted to more than 0.08%, and more preferably to more than 0.10%. On the other hand, the reason why the amount of C is adjusted to 0.50% or less is that when the amount of C exceeds 0.50%, the welding capacity is significantly degraded. Meanwhile, in a case where a welding capacity is more preferably needed, the amount of C is adjusted to 0.25% or less, and more preferably to 0.20% or less.
[0053] Si is an element that increases strength without significantly impairing the forming capacity, particularly the elongation of the steel sheet, and is added to 0.005% to 2.5%. The reason why the amount of Si is adjusted to 0.005% or more is to ensure sufficient tensile strength. Furthermore, in order to stably obtain a tensile strength of 770 MPa or more, the amount of Si is more preferably adjusted to 0.5% or more, and even more preferably to 1.0% or more. The reason that the upper limit on the amount of Si is set to 2.5% or less is that, while the upper limit is within the above range, the effect of increasing resistance is not saturated, and the ductility is not degraded. In particular, in order to obtain favorable weldability and coating properties, the upper limit of Si is more preferably adjusted to 2.0%, and even more preferably to 1.5%.
[0054] In addition, when Si is added four times or more than the amount of C, the progress of the transformation of perlite and bainite is significantly delayed by reheating for a bonding treatment, which is performed immediately after coating, a microstructure in which one or two types of 5% to 70% residual martensite or austenite by area ratio is included in the ferrite even after the steel sheet is cooled to room temperature, and it is easy to guarantee sufficient strength.
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16/71 [0055] The range of the amount of Mn is adjusted to 0.01% to 3.0% in mass%. The lower limit at which the effect of increasing resistance is presented has been adjusted to 0.01%, and the upper limit has been adjusted to 3.0% from the point of view of production costs. Meanwhile, since Mn decreases the free energy of austenite together with C, Mn is more preferably added by 1.5% or more, and even more preferably by 2.0% or more for the purpose of stabilizing the austenite until the steel sheet is immersed in a coating bath. In addition, in a case where Mn is added 12 times or more than the amount of C, the progress of the transformation of perlite and bainite is significantly delayed in reheating for a bonding treatment, which is carried out immediately after coating, once microstructure in which one or two types of 5% to 70% residual martensite or austenite by area ratio is included in the ferrite even after the steel sheet is cooled to room temperature, and it is easy to guarantee sufficient strength. However, when the amount added becomes excessive, since the fracture is liable to occur in the plate, and the weldability is also deteriorated, the upper limit is more preferably adjusted to 2.8% and even more preferably to 2, 5% in a case where strength, conformability, and costs are taken into account.
[0056] Generally, P is included in steel as an unavoidable impurity; however, when the amount of P exceeds 0.03%, the spot welding capacity is significantly deteriorated. In addition, in this case, on a high-strength steel sheet having a tensile strength of more than 770 MPa, as with the modality, both the toughness and the cold rolling properties are significantly deteriorated. Therefore, the amount of P
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17/71 is adjusted to 0.03% or less. A lower amount of P results in a more favorable forming capacity, and the amount of P is more preferably adjusted to 0.02% or less, and even more preferably to 0.01% or less. On the other hand, since reducing the amount of P to less than 0.001% increases refining costs excessively, the lower limit of the amount is adjusted to 0.001%. The amount of P is preferably adjusted to 0.003% to 0.01% in terms of the balance between strength, forming capacity, and costs.
[0057] S is also generally included in steel as an unavoidable impurity, and when its quantity exceeds 0.02%, the expanded MnS in the rolling direction is significantly generated, and the bending properties of the steel sheet are adversely affected. Therefore, the amount of S is limited to 0.02% or less. The amount of S is most preferably adjusted to 0.01% or less, and even more preferably to 0.005% or less. However, it costs money to reduce the amount of S. From the point of view of the forming capacity and adhesion to the plate, it is not necessary to reduce the amount of S excessively, and the amount of S can be reduced to a level necessary for the conditions forming capacity of hot rolling, corrosion resistance, etc.
[0058] N is also generally included in steel as an unavoidable impurity. When the amount of N exceeds 0.0060%, elongation and brittleness are deteriorated, and therefore the amount of N is limited to 0.0060% or less. Particularly, in a case where a favorable forming capacity is required, the amount of N is more preferably adjusted to 0.004% or less, and even more preferably to 0.003% or less. A smaller amount of N is preferred, but reducing the amount to
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18/71 less than 0.0005% increases costs excessively, and therefore the lower limit of the quantity is set to 0.0005%.
[0059] The addition of Al is not essential; however, in a case where Al is added, Al is added as a steel deoxidizing element, and has an effect of refining a hot-rolled material through AlN and suppressing the hardening of the crystal grains in a series of heat treatment processes, thus improving the quality of the material. In a case where this effect is necessary, Al needs to be added to 0.005% or more, and preferably 0.01% or more. However, when more than 0.5% or Al is added, once the costs are increased, and the surface properties are deteriorated, the amount of Al is adjusted to 0.5% or less, preferably to 0.3% or less, more preferably to 0.1% or less, and even more preferably to 0.05% or less.
[0060] In addition, one or more between Ni, Cu, Cr, Mo, B, Ti, Nb, V,
REM (for example, La and Ce), and Ca can be added to steel containing the above elements as main components. Containing these elements does not affect the effects of the modality, and there are also preferable cases in which the resistance or the conformability is improved depending on their quantity. Specifically, the amounts are as follows: Ni: 0.05% to 2.0%, Cu: 0.05% to 2.0%, Cr: 0.05% to 2.0%, Mo: 0.05% 2.0%, B: 0.0001% to 0.002%, Ti: 0.001% to 0.1%, Nb: 0.001% to 0.1%, V: 0.001% to 0.1%, REM: 0, 0001% to 0.1%, and Ca: 0.0001% to 0.1%.
[0061] The addition of Ni, Cu, Cr, and Mo is not essential; however, in a case in which Ni, Cu, Cr, and Mo are added, similarly to Si, there is a tendency to delay the generation of carbides, and the permanence of austenite is helped. In addition, these connection elements decrease the temperature of the start of transformation by
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19/71 austenite martensite. Therefore, the addition of Ni, Cu, Cr, and Mo is effective to increase the forming capacity or the resistance to fatigue. However, in a case where the added amount of each of the connecting elements is less than 0.05%, the above effects are not sufficient, and therefore it is desirable to adjust 0.05% as the lower limit of the added quantities of these elements . On the other hand, when the added amount is increased, once the effect of increasing the resistance is saturated, and the rate of deterioration of the ductility is increased, it is desirable to adjust 2% as the upper limit value of the added amount of each of these elements.
[0062] In addition, when the total added amount of elements Ni, Cu, Cr, and Mo exceeds 3.5%, since the hardening capacity of a steel material is increased more than necessary, it becomes It is difficult to produce a steel sheet that includes mainly ferrite and has a favorable forming capacity, and an increase in steel material costs is caused. Therefore, the upper limit value of the total amount added of the above connecting elements is preferably adjusted to 3.5%. [0063] The addition of B is not essential, but B is known as an element that increases the hardening capacity when added, and it is desirable to add 0.0001% or more of B to delay the transformation into perlite and bainite when it is executed reheating for a bonding treatment. However, when the amount added exceeds 0.005%, since a sufficient area ratio of ferrite is not developed during the cooling of the temperature region of two coexisting ferrite and austenite, and it becomes difficult to produce a steel sheet that includes mainly ferrite and has a favorable forming capacity, it is desirable to set 0.006% as the upper limit value, and it is
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20/71 more desirable to set 0.002% as the upper limit value.
[0064] The addition of Ti, Nb, and V is not essential, but these elements are effective in increasing the strength of a steel sheet since the elements form carbides and nitrides (or carbonitrides), and reinforce the ferrite phase. However, in a case where the added amount of each of these binding elements is less than 0.001%, the above effects are not sufficient, and therefore it is desirable to adjust 0.001% as the lower limit value for the added quantities of these elements. On the other hand, in a case in which more than 0.1% is added, since an increase in costs for a steel material is caused, the effect of increasing strength is saturated, and in addition C is unnecessarily wasted , it is desirable to adjust 0.1% as the upper limit of the added quantity of each element.
[0065] In addition, similarly, in a case where Ti, Nb and V are added in a total of more than 0.20%, since an increase in costs for a steel material is caused, the effect of increasing the resistance is saturated, and also the C is wasted unnecessarily, it is desirable to adjust the value of the upper limit of the total added amount of these connecting elements to 0.2%.
[0066] The addition of REM and Ca is not essential, but REM and Ca combine with S in order to make the inclusions spherical, and improve the ability to work cold or the durability of fatigue. However, in the event that the amount added for each of them is less than 0.0001%, the effects are not sufficient. Therefore, 0.0001% is adjusted as the lower limit of the added quantity. In addition, when these elements are added excessively, once the effects are saturated, and defects in the welded portions are increased, the upper limit value of the added amount of each is adjusted to 0.1%,
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21/71 [0067] Next, the galvanized coated sheet will be described. In the modality, the coated galvanized layer refers to a coated layer that mainly includes an Fe-Zn alloy generated by the dispersion of Fe in the steel during the coating with Zn, which is caused by the bonding reaction. The amount of Fe is adjusted to 1% to 30%. When the amount of Fe in the plate is less than 7% by weight, there are cases in which a soft Fe-Zn alloy is formed on the coated surface, and the cold forming capacity is deteriorated, and when the amount of Fe exceeds 15% en masse, there are cases where a layer of brittle alloy is excessively developed at the ferrite interface, and the adhesion of the plate is deteriorated. Therefore, the amount of Fe is more preferably 7 wt% to 15 wt%.
[0068] In addition, when galvanizing is performed, once Al is added to a coating bath to suppress the bonding reaction in the coating bath, 0.01% to 1.5% by mass of Al is included on the plate. This is because when the amount of Al added is less than 0.01%, sediments of the dominant Zn oxide are generated significantly on the surface of the coating bath, and the appearance after coating is degraded. Since the effect of suppressing the generation of sediments is saturated in the added amount of more than 1.5%, the upper limit was adjusted to 1.5% from the point of view of production costs. The added amount of Al is more preferably 0.05% to 0.50%, and even more preferably 0.10% to 0.30%. In addition, since the diffusion of Fe and the diffusion of elements added to steel occur at the same time in the bonding process, these elements are also included in the plate.
[0069] The adhered quantity of the sheet is not particularly limited, but the single surface thickness is preferably 1 pm
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22/71 or more, and more preferably 3 gm or more from the standpoint of corrosion resistance. In addition, the amount adhered to the single surface is preferably 20 gm or less from the point of view of forming capacity, weldability and economic efficiency.
[0070] Meanwhile, it is within the scope of the modality to coat a top layer or perform a variety of chemical conversion treatments, for example, a phosphate treatment, a weldability improvement treatment, a lubricity improvement treatment, etc. in the coated steel sheet of the modality to improve the painting properties and welding capacity.
[0071] The steel sheet of the modality does not affect the effects of the modality even when the total of 3.5% or less of one or more between Pb, Sb, Si, Sn, Mg, Mn, Ni, Cr, Co, Ca , Cu, Li, Ti, Be, Bi, and rare earth elements are contained or mixed in the galvanizing bath or in the zinc plate and, sometimes, preferably the corrosion resistance or the forming capacity is improved, depending on their quantity . The amount of bonded fused zinc sheet is not particularly limited, but is 20 g / m ² or more from the point of view of corrosion resistance, and preferably 150 g / m ² or less from the point of view of economic efficiency.
[0072] In addition, since the steel sheet of the modality satisfies both high strength and a favorable forming capacity, the single-phase ferrite structure has the maximum area ratio in a complex structure of the microstructure in the steel sheet. The remaining portions of the complex structure are a non-ferrite structure (structures other than the single phase ferrite) having one or more between bainite, martensite, residual austenite, etc. mixed in it. The area ratio of this non-ferrite structure is adjusted
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23/71 to be 5% to 70%. The reason why the microstructure in the steel plate is made of the complex structure above is that it becomes possible to increase the strength while the favorable forming capacity is maintained by reinforcing the soft ferrite with the hard non-ferrite structure. When the area ratio of the hard structure is less than 5%, the effect of increasing strength is not sufficient, and when the area ratio exceeds 70% the forming capacity is significantly deteriorated, and therefore the area ratio of one or more two between martensite and residual austenite are adjusted to be 5% to 70%. In a case where a particularly favorable forming capacity is required, it is preferable to adjust the residual austenite area ratio to 5% or more, and to effectively use TRIP (Transformation-induced plasticity) effect. In a case where a particularly favorable forming capacity is required, the value of the upper limit of the area ratio of the non-ferrite structure is more preferably 50%, and even more preferably 30%.
[0073] Any double-phase steel sheet for which martensite is used as a hard structure, a TRIP steel structure for which the stress-inducing transformation of residual austenite is used, and a steel sheet with complex reinforced structure for which both martensite and residual austenite are used, it can be used as steel sheet with complex reinforced structure. In order to obtain a favorable forming capacity for the steel plate, the ferrite is controlled to have the maximum area ratio. Since a greater area ratio also improves the forming capacity, the area ratio of the ferrite is preferably equal to or 60% to less than 95%. In addition, the steel sheet of the modality is preferably a high strength steel sheet in which the tensile strength TS is 490 MPa and the ratio
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24/71 between the tensile strength TS (MPa) and the elongation (%) satisfies TS x El> 19000. Even more desirable is TS> 590 MPa, and a more preferable one is TS> 770 MPa and TS x El> 20000.
[0074] To obtain a more favorable fatigue life, a microstructure having ferrite at an area ratio of 95% or more can be formed on the side of the steel sheet of the interface between the steel sheet and the galvanized and annealed coated layer. an average thickness (arithmetic mean) of 0.01 qm to 10 qm.
[0075] The reason why the fatigue life is improved by the conformation of the microstructure, in which the ferrite area ratio is 95% or more, at the interface between the steel sheet and the galvanized coated layer, this layer is considered to act as a buffer zone. Since the galvanized and annealed coated layer is hard and brittle, there are cases where the fracture that occurred in the galvanized and annealed coated layer advances on the steel sheet due to the stress of the load, and the steel sheet is finely fractured. On the other hand, when a soft layer (for example, a ferrite layer) is present below the galvanized and annealed coated layer, the fractured ferrite layer is deformed, and the stress concentration is avoided, making it possible to prevent the fracture advances on the steel plate.
[0076] As a result of investigating the relationship between fatigue life and the microstructure of the galvanized and annealed steel sheet using steels having a variety of components, the inventors found that when galvannealing is performed on a steel sheet of complex structure that includes ferrite as the main phase and has one or two phases between martensite and residual austenite at an area ratio of 5% to 30%, a more favorable fatigue life can be obtained by forming a microstructure in which the ratio of ferrite area is 95% or more on the side of the plate
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25/71 steel of the interface between the steel sheet and the coated galvanized and annealed layer with an average thickness of 0.01 μm to 10 μm. [0077] In addition, it is particularly important to adjust the ferrite area ratio in a range of 1 μίτι from just below the plate interface towards the steel plate side to 95% or more to obtain stably the fatigue life. When the ferrite layer is 0.05 μm or more separated from the interface with the coated layer, there are cases where the fatigue life is adversely affected.
[0078] The reason why the average thickness of the microstructure in which the ferrite area ratio is 95% or more is adjusted to 0.01 μm or more is that, in a case where the average thickness of the microstructure in which the ratio ferrite area is 95% or more is less than 0.01 μm, the effect of improving fatigue life is not shown. On the other hand, when the average thickness of the microstructure in which the ferrite area ratio is 95% or more exceeds 10 μm, the effect of improving fatigue life begins to degrade. This is considered to be because, when the microstructure having a ferrite area ratio of 95% or more is thick, the slip that occurred at the edges of the ferrite grains grows while repetitive stresses are loaded, and acts as a starting point for fractures. In contrast to the above, it is considered that in a case in which the average microstructure in which the ferrite area ratio is 95% or more is 10 μm or less, since the slip growth in the graphite grains is significantly suppressed due to the influence of a compressor stress by the galvanized and annealed coated layer having a hard surface, the slip does not act as a starting point for fractures. That is, it is considered that forming a soft microstructure below the galvanized coated layer at an average of 0.01 μm to 10 μm can suppress the
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26/71 occurrence and progression of fractures of the two due to the synergistic effect, and favorable fatigue durability can be obtained. More preferably, when the average thickness of the microstructure in which the ferrite area ratio is 95% or more is adjusted to 3 gm or less, the fatigue life is more stably improved. [0079] Therefore, a higher ferrite area ratio increases the effect of improving fatigue life, and it is desirable to form a microstructure in which the ferrite area ratio is 98% or more and an average thickness of 0.01 gm to 10 gm. In addition, since the thickness of the microstructure in which the ferrite area ratio is not less than 95% or not less than 98% is affected by the thickness of the coated layer, the thickness of the microstructure is preferably twice or less than thickness of the coated layer. The thickness of the microstructure is even more preferably 0.1 gm to 8 gm.
[0080] In the modality, a method of producing the microstructure in which the ferrite area ratio is not less than 95% or not less than 98% is not particularly limited since the microstructure is formed on the side of the steel sheet interface between the steel sheet and the coated galvanized and annealed layer at an average thickness of 0.01 gm to 10 gm.
[0081] To more reliably improve fatigue life, the ferrite area ratio in the portion of the steel plate immediately below the interface of the coated layer, particularly in the portion at a depth of 1 gm or less from the interface with the layer coated is more preferably not less than 95% or not less than 98%.
[0082] The microstructure in which the ferrite area ratio is not less than 95% or not less than 98% can be formed in the surface layer at the same time as a heat treatment is performed to obtain a complex structure having ferrite such as
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27/71 phase of maximum area ratio, and one or more between bainite, martensite and residual austenite mixed there, while the Fe layer having a low carbon concentration is formed in the surface layer of a high strength steel plate before annealing.
[0083] In addition, the microstructure in which the ferrite area ratio is not less than 95% or not less than 98% can be seen from the cross section. Figure 1 shows the results of observing a cross section of a representative steel plate after caustication using an optical microscope. Since the microstructure in which the ferrite area ratio is not less than 95% or not less than 98% has a characteristic that the ferrite grains grow significantly when compared to the complex structure that includes ferrite as the main phase and has one or more between bainite, martensite and residual austenite mixed in it, the microstructure can be easily divided using an optical microscope. In addition, in a case where the fraction of the internal structure is obtained, the fraction can be obtained by observing the structure using a SEM or TEM.
[0084] A method of producing a multilayer steel sheet having a Fe layer having low carbon concentration formed in the surface layer is not particularly limited. It is possible to form a layer of Fe having a low carbon concentration in a plate or in the surface layer of the steel sheet by a variety of methods, such as rolling, cast boning, etc. The cheapest method is to add Fe only to the surface during continuous casting. That is, initially a direct current magnetic field that crosses the thickness of a plate is applied to the feed of molten steel in a continuous casting mold at a location below the meniscus in the direction of
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28/71 casting to form a zone of direct current magnetic field. The molten steel is supplied to a molten steel well on the top side and to a molten steel well on the bottom side which are divided by a direct current magnetic field through two nozzles having different lengths, and the molten steel is solidified. and removed to perform continuous casting. In continuous casting, the concentration of Fe is increased only in the portion of the surface layer by adding Fe to the molten steel well on the top side. As a method of adding Fe, a Fe or Fe alloy in the form of wire and the like can be supplied continuously.
[0085] The multilayer steel sheet plate by the continuous casting method above is processed into a thin sheet by a common method of hot rolling or cold rolling, and then coated in a continuous galvanizing line. The production method of a coated steel sheet is not particularly limited, and a common non-oxidation oven or a full radiant type galvanizing method can be applied. [0086] Furthermore, the steel sheet of the modality has sufficient effects without regard to whether the steel sheet is produced as a cold-rolled steel sheet or a cold-rolled steel sheet by a common process, and the effects do not vary significantly with the history of the steel sheet. In addition, in the modality, the thickness of the steel sheet does not impose any limitation to the modality, and the modality can be applied as long as the steel sheet has a commonly used thickness. The common sheet thickness is between 0.4 mm and 3.2 mm, but is preferably between 1.0 mm and 3.2 mm in consideration of a laminating machine's load or productivity.
[0087] In addition, the hot rolling conditions, the
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29/71 cold rolling conditions, etc., can be appropriately selected according to the dimensions and required strength of the steel sheet, and the effects of the steel sheet of the modality are not affected by the hot rolling conditions, the cold rolling conditions, etc.
[0088] In addition, when annealing is carried out on a continuous galvanizing line, the annealing conditions are that the steel sheet has a complex structure in which the ferrite has the maximum area ratio, and a or more between bainite, martensite, and residual austenite are mixed as the microstructure, and the selected conditions allow to obtain a complex structure in which the area ratio of one or two between martensite and residual austenite is 5% to 70%.
[0089] Specifically, annealing is carried out in the region of two coexisting phases of ferrite and austenite from 700 ° C to 850 ° C, and cooling is carried out from the peak temperature to 650 ° C at an average rate of 0, 5 ° C / s to 10 ° C / s, and subsequently from 650 ° C to the coating bath at an average rate of 1 ° C / s to 20 ° C / s. As described above, as long as a layer of Fe having a low carbon concentration is formed in the surface layer of the high strength steel plate before annealing, at the same time, it becomes possible to form a microstructure in which the area ratio of the ferrite is not less than 95% or not less than 98% in the surface layer during heat treatment.
[0090] As the temperature of the plating bath for galvanizing, the condition of the relative technique can be applied. For example, the 440 ° C to 550 ° C condition can be applied. In addition, in a case where a galvanized and annealed steel sheet is produced by performing galvanization and then
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30/71 heating connection, the condition in the relative art can be applied as the heating temperature for connection, for example, the condition of 400 ° C to 600 ° C can be applied. The heating method for connection is not particularly limited, a heating method corresponding to a galvanizing line in the relative art, such as direct heating using a flue gas, induction heating, or direct resistance heating, can be used .
[0091] After bonding treatment, the steel sheet is cooled to 200 ° C or less, and subjected to hardening lamination according to need. The cooling rate after bonding can be selected depending on the desired microstructure, a large cooling rate can be selected to promote the concentration of C in the residual austenite by transforming austenite into bainite and, consequently, producing residual austenite. [0092] The coated steel sheet produced was cut in the thickness direction, and the hardness of the steel sheet was measured in a cross section by the nano-recess method in the vicinity immediately below the plate / ferrite interface and in the vicinity of a depth 1/3 of the thickness of the steel sheet. As a measuring equipment, an atomic force microscope was used using an incision-causing diamond having the shape of a triangular pyramid at the front end (produced by Shimadzu Corporation, SPM-9500). The load on the incision maker has been adjusted so that the depth of the incision in the direction of the inner layer becomes 5 nm. The hardness of the steel plate was measured at locations with a depth of 10 nm along the direction of the thickness of the steel plate, five points for each depth were measured, and an average hardness was obtained for each of the depth locations. In the present specification, the hardness of the steel sheet
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31/71 measured by the above method is called nano-hardness. Nano hardness at a depth of 1/3 of the thickness of the steel plate is defined as the representative nano hardness (Ha) inside the steel plate, and hereinafter described as the nano hardness inside the steel plate. Using nano hardness inside the steel plate as the standard value, the portion immediately below the steel plate coating interface, in which the nano hardness is 75% or less of the standard value, was defined as the softened layer ( soft layer or soft layer of the interface). In summary, the measured values of the nano hardness of the steel sheet at 10 nm in the direction of the thickness immediately below the coating interface are scanned, and until the portion in which the measured value that exceeded 75% of the standard value is initially detected are considered be the softened layer.
[0093] This depth becomes the depth D (pm) of the softened layer. Meanwhile, in a case where the average values of nano hardness measured in five layers from 10 nm to 50 nm deep just below the coating interface, it was determined that there was no soft layer, and the average value above was recorded as the hardness of the surface layer.
[0094] In a case in which the depth D of the softened layer on the coated steel sheet was 0.001% to 5% of the thickness t of the steel sheet portion, the fatigue durability particularly showed a favorable value stably. In a case where D did not reach 0.001% t, the fatigue life became poor and, in a case where D exceeded 5% t, there were cases where a problem occurred with the strength of the coated steel sheet.
[0095] The concentration of C in the surface layer was measured as follows:
(In a case where the softened layer D is 0.1 pm to 5 pm)
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32/71 [0096] After only the coated layer is dissolved and removed using an aqueous HCl solution containing 30% by mass of an inhibitor, the front and rear surfaces of the ferrite are dissolved by D gm using based on weight method in which the reduced amount of thickness is assessed using the weight before and after blasting as indices. Next, in relation to the dry substance obtained by vaporizing and drying the dissolution fluid, the amount of C is determined using the infrared absorption method after combustion of Standard JIS G1211.
(In a case where the softened layer D exceeds 5 gm) [0097] After only the coated layer is dissolved and removed using an aqueous HCl solution containing 30% by mass, the front and rear surfaces of the ferrite are dissolved by 5 gm using an aqueous solution of HCl 5% by mass at 60 ° C based on the weight method in which the reduced amount of thickness is evaluated using the weights before and after blasting as indices. Next, in relation to the dry substance obtained by vaporizing and drying the dissolution fluid, the amount of C is determined using the infrared absorption method after combustion of Standard JIS G1211.
(In a case where the softened layer D is less than 0.1 gm) [0098] Weights are determined at 5 arbitrary points in a cross section of the ferrite surface layer using an FE-EPMA having a probe diameter 0.1 gm, and its average value is obtained. However, since the probe diameter is larger than the softened layer D, the measured values are used as reference values, [0099] Meanwhile, to maintain sufficient strength of the steel plate even when the softened layer exists, the C concentration in the softened layer is preferably 10% at
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33/71 less than 30% in relation to the C concentration in the entire steel plate. When the C concentration in the softened layer becomes 10% or less of the C concentration in the entire steel sheet, the softened layer becomes softer than necessary, and there are cases where the strength of the steel sheet is adversely affected .
[Example 1] [00100] Hereinafter the modality will be described specifically using an example.
[00101] The continuous casting was performed in a continuous casting equipment provided with an electromagnetic brake and a wire supply equipment to add an alloy to the molding section, thus obtaining steels having the composition as shown in Table 1. The electromagnetic force of the electromagnetic brake was set to 0.1 T to 1.0 T, and an Fe wire was used. The added amount of Fe wire was adjusted using the cross-sectional area and the iron wire supply rate.
[00102] Next, plates were produced as above and had an increased concentration of Fe in the portion of the surface layer were hot rolled at a heating temperature of 1080 ° C to 1150 ° C, a finishing finish temperature of 910 ° C to 930 ° C, and a winding temperature of 580 ° C to 690 ° C, thus making a steel sheet having a thickness of 4.0 mm. In addition, the sheets were stripped, then cold rolled to 2.0 mm thick, and plated on a continuous plating line. During the annealing process on the continuous galvanizing line, the peak temperature was 760 ° C to 830 ° C, the average cooling rate from the peak temperature to 650 ° C was 1 ° C / s to 5 ° C / s, and the average cooling rate of 650 ° C to the coating bath was 3 ° C / s
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34/71
12 ° C / s. The molten zinc plate was coated in a galvanizing bath having a coating bath temperature of 460 ° C and containing 0.13% Al, and the adhered quantity of the plate was adjusted to 50 g / m ² using nitrogen and gas drying.
[00103] Tensile strength and elongation were measured by cutting a JIS No. 5 specimen from the coated steel zone as above and performing a tensile test at room temperature.
[00104]% Fe and% Al on the plate were measured by ICP after the coating was dissolved in an inhibitor containing hydrochloric acid. The% of Fe was 10% to 11% on average, and the% of Al was 0.2% to 0.3% on average. The adhered quantity of the plate was obtained from the difference in weight before and after the dissolution of the coating. The amount of coating adhered was 45 g / m ² to 55 g / m ² on average. In addition, the thickness of the plate was observed from the cross section using an SEM, and the thickness of the plate was 6.3 qm to 7.7 qm on average.
[00105] The type and volume of the microstructure inside and in the surface layer of the steel plate were observed using an optical microscope having a magnification of 400 times to 1000 times and an SEM having a magnification of 1000 times to 100000 times as the cross section of the steel sheet in the rolling direction or a cross section in the 90 ° direction of the rolling direction was etched using a Nital reagent and the reagent as described in the unexamined Japanese Patent Application, first publication no. S59 -219473. In addition, the type and volume of the microstructure inside and on the surface layer of the steel plate were also observed using an FE-TEM having a magnification of 10000 times to 1000000 times as the cross section sample is produced by FIBq sampling method.
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Twenty or more locations were observed in each of the samples. In addition, the area ratio was specified by the method of counting points or an image analysis. The average thickness of the microstructure in which the ferrite area ratio was 95% or more was also similarly observed using an optical microscope having a magnification of 1000 to 100000 times according to the cross section of the steel sheet in the direction of lamination or the cross section in the 90 ° direction of the lamination direction was etched using a Nital reagent and the reagent as described in the unexamined Japanese Patent Application, first publication No. S59-219473. In addition, the thickness of a thin sample was also observed using an FE-TEM having a magnification of 10000 times to 1000000 times as the cross section sample was produced by the FIBg sampling method.
[00106] The fatigue durability was evaluated using limits of fatigue ratios for the tensile strength (fatigue ratios). In the specification, the limit fatigue ratio for tensile strength is a value of 2 χ 10 ⁷ resistance to time, which is obtained by performing a fatigue test according to JIS Z 2275 on test specimen No. 1 as defined on JIS Z 2275 having a parallel portion of 30 mm, a sheet thickness of 2 mm, and a radius of curvature of 100 mm, divided by tensile strength. Steel sheets having a limit fatigue ratio for tensile strength above 0.7 0.0003 χ TS were assessed as acceptable.
[00107] The results are gathered in Table 2. The microstructure column shows the area ratios of Ferrite (F), bainite (B), martensite (M), residual austenite (γ), and other structures. In addition, the combined area ratio of martensite (M) and residual austenite (γ) is shown. The coated steel sheet ^Nos 1, 2, 4, 27, 28, and 29 have lower resistance to draw than 770 MPa, which is outside the
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36/71 mode track. The coated steel sheets ^Nos 30, 31, and 32 failed to satisfy the desired range in thickness softened layer (surface layer) which was measured by the nano hardness. In these steels, the values of the limit fatigue ratio for the tensile strength were also below the target value. In products of the modality other than the above, a favorable fatigue life can be obtained stably.
[00108] In addition, as a result of measuring the C concentrations in the surface layer of each of the coated steel sheets produced according to the modality, the C concentration in the steel sheet was maintained in a range of 10% to 30% on all samples.
[Example 2] [00109] Continuous casting was performed on a continuous casting machine provided with an electromagnetic brake and wire supply equipment to add an alloy to the molding section, and a plate having the composition as shown in column J from Table 1 was produced. The electromagnetic force of the electromagnetic brake was adjusted to 0.1 T to 1.0 T, and an Fe wire was used. The added amount of Fe wire was adjusted using the cross-sectional area and the rate of supply of the Fe Fe wire.
[00110] Next, the plate that was produced in the above manner and had a variety of Fe thicknesses concentrated in the portion of the surface layer was hot rolled at a heating temperature of 1080 ° C to 1150 ° C, a temperature of finish finishing laminate from 910 ° C to 930 ° C. and a winding temperature of 580 ° C to 690 ° C, thus producing a sheet thickness of 4.0 mm. In addition, the plate was stripped, then cold rolled to a thickness of 2.0 mm, and subjected to
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37/71 galvanizing on a continuous galvanizing line. In the continuous galvanizing line, the peak temperature was 800 ° C, the average cooling rate from the peak temperature to 650 ° C was 2 ° C / s, and the average cooling rate of 650 ° C until the coating bath was 5 ° C / s. The molten zinc coating was coated in a galvanizing bath having a galvanizing bath temperature of 460 ° C and containing 0.13% Al, and the adhered amount of the plate was adjusted to 35 g / m ² by gas drying. nitrogen. The bonding temperature of the coating was adjusted to 500 ° C.
[00111] In addition, as a comparative material, an annealing simulator was used using an infrared image furnace, and a heat treatment that simulated the continuous galvanizing line was performed in an N2 gas atmosphere. In the annealing simulator, the peak temperature was 800 ° C, the average cooling rate from the peak temperature to 650 ° C was 2 ° C / s, and the average cooling rate from 650 ° C to 460 ° C was 5 ° C / s. The connection temperature of the plate was set to 500 ° C.
[00112] Tensile strength and elongation were measured by cutting a JIS No. 5 specimen from the area of the coated sheet produced in the above manner and performing a tensile test at room temperature.
[00113]% Fe and% Al in the coating were measured by ICP after the coating was dissolved in an inhibitor containing hydrochloric acid. The% of Fe was 10% to 11% on average, and the% of Al was 0.2% to 0.3% on average. The adhered amount of the coating was obtained from the difference in weight before and after the coating dissolved. The adhered amount of the plate was 30 g / m ² to 40 g / m ² on average. In addition, the thickness of the coating was observed from the cross section using a SEM, and the thickness of the
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38/71 coating was 4.2 pm to 5.6 pm on average.
[00114] The type and volume of the microstructure inside and on the surface layer of the steel plate were observed using an optical microscope having a magnification of 400 times to 1000 times and an SEM having a magnification of 1000 times to 100000 times depending on the cross section of the steel sheet in the rolling direction or the cross section in the 90 ° direction of the rolling direction was etched using a Nital reagent and the reagent as described in the unexamined Japanese Patent Application, first publication no. S59-219473. In addition, the type and volume of the microstructure inside and on the surface layer of the steel plate were also observed using an FE-TEM having a magnification of 10000 times to 1000000 times after the cross section sample was produced by FIBp sampling method. Twenty or more sites were observed in each of the samples. In addition, the area ratio was obtained by the method of counting points or image analysis.
[00115] Similarly, the average thickness of the microstructure in which the ferrite area ratio is 95% or more was also observed using an optical microscope having a magnification of 400 times to 1000 times and an SEM having a magnification of 1000 times at 100000 times in the cross section of the steel sheet in the rolling direction or in the cross section in the 90 ° direction of the rolling direction was etched using a Nital reagent and a reagent as described in the unexamined Japanese Patent Application, first publication No. S59-219473. In addition, the thickness of a thin sample was also observed using an FE-TEM having a magnification of 10000 times to 1000000 times after the cross section sample was produced by the FIBp sampling method.
[00116] Fatigue durability was assessed using ratios of
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39/71 fatigue limits for tensile strength. In the specification, the limit fatigue ratio for the tensile strength is a value of 2 χ 10 ⁷ times the resistance, which is obtained by performing a fatigue test according to JIS Z 2275 on the specimen No. 1 as defined in JIS Z 2275 having a parallel portion of 30 mm, a sheet thickness of 2 mm, and a radius of curvature of 100 mm, divided by tensile strength. Steel sheets having a limit fatigue ratio for the tensile strength above 0.7 - 0.0003 x TS were evaluated as acceptable.
[00117] The results are shown in Table 3. Since the average thickness of the microstructures in which the ferrite area ratio was 95% or more were outside the range of the mode of paragraphs 1 to 12, the fatigue limit ratios for tensile strength they were below 0.7 - 0.0003 x TS. Since the ferrite area ratio in the surface layer was outside the modality range at No. 14, the limit fatigue ratio for tensile strength was below 0.7 - 0.0003 x TS. For No. 15 that was not coated, the limit fatigue ratio for the tensile strength was above 0.7 - 0.0003 x TS even when the average thickness of the microstructure in which the ferrite area ratio was 95% or more was out of the modality range; however, conversely, to ^points 16, 17 and 18 in which the microstructures having a ferrite area ratio of 95% or more becomes thick, the reasons of fatigue limit to the tensile strength were below 0.7 - 0.0003 x TS.
[00118] The products of the modality different from the above were high strength galvanized steel sheets that can stably produce favorable fatigue durability.
[00119] In addition, as a result of measuring the concentration of C in the surface layer of each of the coated steel sheets produced according to the modality, the concentration of C in the
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40/71 steel plate was maintained in a range of 10% to 30% in all samples, except sample no. 2.
Table 1 (1/2)
Symbol Chemical Components (% by mass) Ç Si Mn P s Al N THE 0.073 0.54 2.18 0.011 0.0020 0.035 0.0030 B 0.123 0.72 1.67 0.007 0.0024 0.450 0.0029 Ç 0.141 1.03 2.03 0.009 0.0022 0.027 0.0042 D 0.081 0.12 1.55 0.009 0.0023 0.031 0.0026 AND 0.121 0.82 2.27 0.008 0.0020 0.054 0.0034 F 0.141 1.32 1.79 0.011 0.0021 0.031 0.0027 G 0.176 1.24 2.50 0.009 0.0024 0.025 0.0022 H 0.200 1.50 1.50 0.008 0.0022 0.037 0.0028 I 0.230 1.80 1.50 0.007 0.0023 0.032 0.0031 J 0.100 0.69 2.32 0.009 0.0040 0.044 0.0033 K 0.095 0.72 2.33 0.007 0.0021 0.033 0.0022 L 0.104 0.70 2.25 0.009 0.0024 0.029 0.0025 M 0.098 0.74 2.32 0.009 0.0022 0.025 0.0023 N 0.101 0.66 2.30 0.008 0.0023 0.031 0.0021 O 0.096 0.73 2.28 0.007 0.0022 0.024 0.0024 P 0.103 0.69 2.34 0.008 0.0023 0.026 0.0022 Q 0.099 0.67 2.26 0.007 0.0021 0.033 0.0023 R 0.096 0.72 2.31 0.009 0.0024 0.030 0.0025 s 0.102 0.68 2.35 0.009 0.0022 0.028 0.0021 T 0.099 0.65 2.27 0.009 0.0023 0.027 0.0024 U 0.101 0.71 2.34 0.009 0.0021 0.034 0.0023 V 0.098 0.66 2.26 0.008 0.0024 0.025 0.0022 W 0.103 0.68 2.30 0.007 0.0021 0.032 0.0021 X 0.097 0.70 2.29 0.009 0.0024 0.027 0.0024
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Symbol Chemical Components (% by mass) Ç Si Mn P s Al N Y 0.105 0.69 2.32 0.009 0.0022 0.031 0.0025 Z 0.100 0.74 2.28 0.008 0.0023 0.029 0.0023 A2 0.020 0.73 1.87 0.006 0.0040 0.045 0.0023 B2 0.070 0.19 1.76 0.007 0.0030 0.034 0.0031 C2 0.070 0.64 0.95 0.009 0.0040 0.029 0.0040 D2 0.143 0.76 2.08 0.009 0.0026 0.037 0.0028 E2 0.105 0.76 2.15 0.008 0.0022 0.031 0.0023 F2 0.104 0.68 2.32 0.007 0.0023 0.029 0.0024
Table 1 (2/2)
Symbol Chemical Components (% by mass) Ni Ass Cr Mo Nb You V Here REM B THE B Ç D AND F G H I J K 0.80L0.80 M 0.80 N 0.60 O 0.02P0.02
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Symbol Chemical Components (% by mass) Ni Ass Cr Mo Nb You V Here REM B Q 0.02 0.02 R0.01 0.05 s 0.003 T 0.01U0.002 V 0.42 0.02 W 0.500.01 0.02 X 0.02 0.01 Y 0.20 0.03 Z 0.600.04 0.02 A20.001 B20.002 C20.002 D2 E2 0.02 0.03 F2 0.45
Table 2 (1/2)
No. Steel plate symbol Propr. steel sheet material Microstructure in steel sheet F insurface layer YP TS El F B M y Others M + y (MPa) (MPa) (%) (%) (%) (%) (%) (%) (%) (%) 1 THE 371 607 33 919 9 97 2 B 395 604 38 89 5 1 56 97 3 Ç 448 805 28 78 10 2 1012 95 4 D 389 621 36 90 4 2 46 98 5 AND 427 788 27 8415 116 95 6 F 462 824 31 78 111111 93
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No. Symbol of Propr. steel sheet material Microstructure in steel sheet F inlayer of 7 G 485 872 29 74 12 2 1214 94 8 H 735 907 33 65 16 3 1619 91 9 I 764 976 33 61 18 3 1821 91 10 J 471 777 27 8218 18 95 11 K 589 907 23 7723 23 92 12 L 581 892 23 7822 22 91 13 M 595 916 23 7524 125 92 14 N 587 924 24 7424 226 93 15 O 534 822 26 8218 18 95 16 P 531 817 26 8218 18 94 17 Q 558 858 24 8218 18 92 18 R 537 826 25 8218 18 95 19 s 472 781 27 8218 18 94 20 T 468 778 27 8218 18 95 21 U 548 843 25 7921 21 94 22 V 570 877 24 7921 21 93 23 W 597 918 23 7822 22 93 24 X 573 882 24 8020 20 93 25 Y 607 934 22 7723 23 92 26 Z 694 1069 19 7425 126 91 27 A2 296 423 38 100 0 99 28 B2 321 459 34 90 1 9 0 99 29 C2 308 431 35 91 9 0 99 30 D2 441 816 26 82 1 18 18 96 31 E2 555 843 25 8019 120 92 32 F2 578 906 24 7523 225 93
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Table 2 (2/2)
No. Steel plate symbol C insurface layer (% inpasta) Layer thicknesssurface (mm) Fatigue ratio Nano hardness Note Steel sheet interior (GPa) Surface layer (GPa) Surface / interior layer 1 THE 0.022 0 0.57 3.02 2.74 0.91 Ex. Comp. 2 B 0.035 0 0.57 3.01 2.71 0.90 Ex. Comp. 3 Ç 0.037 3.8 0.51 4.17 2.81 0.67 Ex. Inv. 4 D 0.020 0 0.56 3.05 2.67 0.88 Ex. Comp. 5 AND 0.033 4.1 0.51 4.00 2.82 0.71 Ex. Inv. 6 F 0.041 8.6 0.5 4.39 2.87 0.65 Ex. Inv. 7 G 0.045 5.7 0.49 5.04 2.83 0.56 Ex. Inv. 8 H 0.059 1.2 0.48 5.65 2.94 0.52 Ex. Inv. 9 I 0.062 9.4 0.46 7.16 2.93 0.41 Ex. Inv. 10 J 0.026 0.8 0.51 3.90 2.78 0.71 Ex. Inv. 11 K 0.027 6.1 0.48 5.64 2.91 0.52 Ex. Inv. 12 L 0.031 5.9 0.48 5.37 2.94 0.55 Ex. Inv. 13 M 0.028 2.2 0.48 5.81 2.93 0.50 Ex. Inv. 14 N 0.027 7.8 0.47 5.97 2.89 0.48 Ex. Inv. 15 O 0.024 0.5 0.49 4.36 2.79 0.64 Ex. Inv. 16 P 0.028 4.6 0.5 4.30 2.84 0.66 Ex. Inv. 17 Q 0.029 1.4 0.49 4.83 2.90 0.60 Ex. Inv. 18 R 0.024 9.5 0.5 4.41 2.81 0.64 Ex. Inv. 19 s 0.030 3.7 0.55 3.93 2.85 0.73 Ex. Inv. 20 T 0.027 8.3 0.55 3.91 2.8 0.72 Ex. Inv. 21 U 0.026 4.2 0.5 4.63 2.83 0.61 Ex. Inv. 22 V 0.027 7.6 0.49 5.12 2.89 0.56 Ex. Inv.
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No. Symbol C in Thickness Reason Nano hardness Note 23 W 0.027 6.8 0.47 5.85 2.87 0.49 Ex. Inv. 24 X 0.027 2.9 0.49 5.20 2.88 0.55 Ex. Inv. 25 Y 0.028 8.4 0.47 6.17 2.89 0.47 Ex. Inv. 26 Z 0.025 3.5 0.43 10.08 2.94 0.29 Ex. Inv. 27 A2 0.007 0 0.61 2.83 2.66 0.94 Ex. Comp. 28 B2 0.018 0 0.59 2.85 2.66 0.93 Ex. Comp. 29 C2 0.019 0 0.62 2.84 2.65 0.93 Ex. Comp. 30 D2 0.048 0.05 0.45 4.03 2.99 0.74 Ex. Comp. 31 E2 0.031 11.7 0.44 4.75 2.51 0.53 Ex. Comp. 32 F2 0.025 0 0.42 5.87 4.59 0.78 Ex. Comp.
Table 3 (1/2)
No. Steel plate symbol Propr. steel sheet material Microstructure in steel sheet F insurface layer(%) Thick. of the surface layer (mm) YP(MPa) TS(MPa) El(%) F(%) B(%) M(%) y(%) M + y(%) 1 J 471 777 27 821818 - 0 2 J 472 777 27 821818 96 0.05 3 J 471 778 27 821818 96 0.1 4 J 470 776 27 821818 96 0.3 5 J 471 777 27 821818 95 0.5 6 J 471 776 27 821818 96 0.8 7 J 470 777 27 821818 96 1 8 J 471 778 27 821818 96 3 9 J 472 777 27 821818 95 5 10 J 471 777 27 821818 96 8 11 J 471 777 27 821818 96 10 12 J 471 776 27 821818 96 20 13 J 470 777 27 821818 90 1.5
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No. Steel plate symbol Propr. steel sheet material Microstructure in steel sheet F insurface layer(%) Thick. of the surface layer (mm) YP(MPa) TS(MPa) El(%) F(%) B(%) M(%) y(%) M + y(%) 14 J 471 777 27 821818 85 1.5 15 J 473 783 27 821818 - 0 16 J 472 783 27 821818 95 0.5 17 J 473 784 27 821818 96 1 18 J 474 783 27 821818 95 5
Table 3 (2/2)
No. Steel plate symbol Surface layerÇ Coating Fatigue ratio Nano hardness Note (% inpasta) Steel sheet interior (GPa) layer ofsurface (GPa) surface / interior layer 1 JGift 0.42 3.90 - - Ex. Comp. 2 J 0.490 Gift 0.48 3.89 2.78 0.71 Ex. Inv. 3 J 0.026 Gift 0.5 3.91 2.77 0.71 Ex. Inv. 4 J 0.024 Gift 0.51 3.88 2.79 0.72 Ex. Inv. 5 J 0.025 Gift 0.51 3.90 2.78 0.71 Ex. Inv. 6 J 0.027 Gift 0.51 3.89 2.78 0.71 Ex. Inv. 7 J 0.026 Gift 0.52 3.87 2.79 0.72 Ex. Inv. 8 J 0.026 Gift 0.52 3.9 2.80 0.72 Ex. Inv. 9 J 0.026 Gift 0.52 3.88 2.77 0.71 Ex. Inv. 10 J 0.026 Gift 0.52 3.86 2.78 0.72 Ex. Inv. 11 J 0.026 Gift 0.49 3.92 2.78 0.71 Ex. Inv.
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No. Steel plate symbol Surface layerÇ Coating Fatigue ratio Nano hardness Note (% inpasta) Steel sheet interior (GPa) layer ofsurface (GPa) surface / interior layer 12 J 0.026 Gift 0.45 3.87 2.79 0.72 Ex. Comp; 13 J 0.026 Gift 0.5 3.89 2.76 0.71 Ex. Inv. 14 J 0.026 Gift 0.44 3.90 2.78 0.71 Ex. Comp. 15 JAbsent 0.47 3.96 - - Ex. Comp. 16 J 0.026 Absent 0.46 3.95 2.77 0.70 Ex. Comp. 17 J 0.026 Absent 0.45 3.96 2.78 0.70 Ex. Comp. 18 J 0.026 Absent 0.44 3.94 2.76 0.70 Ex. Comp.
(Second embodiment) [00120] Hereinafter, a second embodiment of the present invention will be described in detail. Initially, the reason why the components of the steel plate used in the modality are limited will be described.
[00121] The reason why the C quantity range has been adjusted to 0.10% to 0.50%, in% by mass, is that the lower limit of the C quantity has been adjusted to 0.10% to ensure resistance , and 0.50% was set as the upper limit at which the welding capacity can be maintained. The reason that the Si amount range has been adjusted to 0.005% to 2.0%, in mass%, is that the lower limit of the Si amount has been adjusted to 0.005% to ensure resistance, and the upper limit has been adjusted to 2.0%, in which the weldability and coating properties are not adversely affected.
[00122] The reason why the Mn amount range has been adjusted
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[00123] P, S, Al, and N are inevitably contained as other elements reached from the above. One or more elements between Ti, Nb, Mo, W, Co, Cu, Cr, Ni, Sn, V, B, and REM can be contained in a range of 0% to 3.5% in total according to the need .
[00124] Next, the reason why the galvanized coated layer used in the modality is limited will be described.
[00125] The reason why the range of the amount of Al in the coated layer is less than 0.01% to 1.5%, in% by mass, is that when the amount of Al is less than 0.01%, Dominant zinc oxide is generated significantly on the surface of the coating bath, and the appearance after coating is degraded. Since the effect of suppressing the generation of waste is saturated when the amount of Al exceeds 1.5%, the upper limit was adjusted to 1.5% from the point of view of production costs.
[00126] The adhered quantity of the sheet is not particularly limited, but is preferably 1 gm or more in the thickness of a punic surface from the point of view of corrosion resistance. In addition, the amount adhered to a single surface is preferably 20 gm or less from the point of view of forming capacity, weldability, and economic efficiency.
[00127] Meanwhile, it is still within the scope of the modality to coat a top layer or perform a variety of chemical conversion treatments, for example, a phosphate treatment, a weldability improvement treatment, an improve treatment lubricity, etc. on coated steel sheet
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49/71 of the modality to improve the painting properties and the welding capacity.
[00128] The sheet thickness range t (mm) excluding the coated layer is not particularly limited. The sheet thickness range t is ordinarily between 0.4 mm to 3.2 mm, but is preferably between 1.0 mm and 3.2 mm in consideration of the productivity or the load of the laminating machine.
[00129] The measurement by the nano-indentation method was performed by the same method as in the first modality. As a result, when the thickness of the softened layer (also expressed as a surface layer) on the ferrite portion of the steel plate from the coating / ferrite interface was indicated by D (mm), and the thickness of the entire steel plate excluding the coated layer was indicated by t (mm), the preferred range of D was adjusted to 0.001% to 5% t. D in the above range has an effect of improving the resistance to hydrogen embrittlement of the steel sheet. Its detailed reason is not clear, but the presence of the soft layer in the surface layer is considered to affect resistance to hydrogen embrittlement. In addition, when the thickness D of the softened layer exceeds 5% t, the strength of the entire steel sheet is degraded, and therefore 5% has been adjusted as the upper limit value.
[00130] Meanwhile, to maintain sufficient strength of the steel sheet even when the softened layer is present, the C concentration in the softened layer is preferably 10% to less than 30% of the C concentration of the entire steel sheet. When the C concentration in the softened layer becomes 10% or less of the C concentration in the entire steel sheet, the softened layer becomes softer than necessary, and there are cases where the strength of the sheet is adversely affected.
[00131] The reason why the D range is adjusted to d / 4 <D <2d
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50/71 when the depth of the coating / ferrite interface in which oxides, including one or two between Si and Mn, which are present in the steel, is indicated by d (pm) is that the resistance to hydrogen embrittlement is more favorable in the range above. The detailed reason is not clear, but it is considered that the above fact results from the effect of the oxides present in this range to suppress the spread of fractures.
[00132] The sizes of the oxides including one or two between Si and Mn that are present in the steel are not particularly limited, but the average diameter preferably does not exceed 1 pm so that the elongation is not degraded, and is preferably 5 nm or more to suppress the promotion of fractures. In addition, the oxide shape can be any spherical shape, a plate shape, a needle shape, etc. The number of oxides is not particularly limited, but it is preferable that one or more oxides are present over a length of 100 pm in the direction of the thickness of the plate in a cross section at a depth of d (pm) when observing the cross section.
[00133] The reason why the tensile strength of the steel sheet is set to 770 MPa or more is that, at a tensile strength of less than 770 MPa, the hardness of the steel material is less than 3.5 GPa, inclusive on the surface, and therefore there is no problem of occurrence and propagation of fractures in the steel material due to embrittlement by hydrogen.
[00134] The relationship between the thickness D of the soft layer (softened layer) in which the nano hardness generated at that moment is 75% or less than that inside the steel sheet and the depth d of the layer with generated oxide is preferably D> d from the point of view of suppressing the spread of fractures, [00135] The method of producing galvanized steel sheet which is excellent in terms of embrittlement resistance will be described
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[00136] A steel plate containing, in mass%, C: 0.10% to 0.50%, Si: 0.005% to 2.0%, Mn: 0.01% to 3.0% with the rest composed of Fe and the inevitable impurities carefully directed to a continuous, produced galvanizing line. When the steel sheet is annealed on the continuous galvanizing line, the peak temperature of the sheet during annealing is 650 ° C to 900 ° C .. When the peak sheet temperature is adjusted to be in a range of 750 ° At 850 ° C, favorable resistance to embrittlement by hydrogen is likely to be achieved stably, which is preferable.
[00137] In addition, when the annealing atmosphere at the peak plate temperature is controlled to contain, in% by volume, 1% to 10% of hydrogen with remaining nitrogen compound and the inevitable impurities and has a higher dew point than 0 ° C to 50 ° C, it becomes possible to form a predetermined thickness of a layer in which the nano hardness is 75% or less than that of the inside of the steel sheet on the surface of the steel sheet, thus allowing the stable obtaining of resistance to hydrogen embrittlement. When the hydrogen in the annealing atmosphere is controlled in a range of 2% to 8%, in% by volume, there is a tendency for the favorable resistance to hydrogen embrittlement to be obtained more stably, which is preferable. Since the generation of Si oxides is suppressed on the surface of the steel sheet after annealing, the wetting properties are also favorable.
[00138] The retention time at the peak temperature of the plate depends on the mechanical properties required for the steel plate, and thus is not particularly limited to a certain range; however, it is generally preferable to select the required retention time to obtain the necessary mechanical properties of 10
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52/71 seconds to 20 minutes. The retention time is preferably between 20 seconds and 150 seconds from the point of view of productivity. [00139] The annealed steel sheet is cooled to a range of 350 ° C to 550 ° C, immersed in a coating bath from 440 ° C to 480 ° C, taken from the bath, controlled to have a predetermined amount of coating, and cold.
[Example 3] [00140] In the following, the example of the modality will be described, but the conditions in the example are an example of the conditions used to confirm the feasibility and effects of the modality, and the modality is not limited to the example of the conditions. The modality can employ a variety of conditions within the essence of the modality as long as the objective of the modality is achieved.
[00141] Other elements that are not shown in Table 4 are not added, but included in the steel only in small quantities as unavoidable impurities.
[00142] Steel sheets having the steel components and sheet thicknesses shown in Table 4 were subjected to an annealing treatment at annealing temperatures, hydrogen concentrations, and dew points as shown in Table 5, immersed in a bath coating of molten Zn at a bath temperature of 450 ° C for 3 seconds, removed from the bath, controlled to have an amount adhered to a single surface of 1 gm to 20 gm by gas drying, and subsequently subjected to a treatment for cool to room temperature using nitrogen gas. After the coating obtained on the coated steel plate was dissolved by an acid, the results of the chemical analysis were as shown in Table 5 as Al (%) on the plate.
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Table 4
N ° steel sheet C in steel (%) Si in steel (%) Mn in steel (%) Thick. of plate t (mm) S1 0.10 0.01 0.50 1.20 S2 0.15 0.10 0.10 1.60 S3 0.20 0.10 0.50 1.80 S4 0.25 0.10 1.00 2.00 S5 0.30 0.50 2.00 2.30 S6 0.40 0.50 3.00 2.70 S7 0.50 0.50 0.01 3.20 S8 0.10 1.00 0.10 1.00 S9 0.15 1.00 0.50 1.60 S10 0.20 1.00 1.00 1.80 S11 0.25 2.00 2.00 2.00 S12 0.30 2.00 3.00 2.30 S13 0.40 2.00 0.01 2.70 S14 0.50 0.01 0.10 3.20 S15 0.10 0.10 0.50 1.20 S16 0.15 0.10 1.00 1.60 S17 0.20 0.10 2.00 1.80 S18 0.25 0.50 3.00 2.00 S19 0.30 0.50 0.01 2.30 S20 0.40 0.50 0.10 2.70 S21 0.50 1.00 0.50 3.20 S22 0.10 1.00 1.00 1.20 S23 0.15 1.00 2.00 1.60 S24 0.20 2.00 3.00 1.80 S25 0.25 2.00 0.01 2.00 S26 0.30 2.00 0.10 2.30 S27 0.40 0.01 0.50 2.70
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N ° steel sheet C in steel (%) Si in steel (%) Mn in steel (%) Thick. of plate t (mm) S28 0.50 0.10 1.00 3.20 S29 0.20 1.20 1.50 1.00 S30 0.05 0.10 0.50 1.80
Table 5 (1/3)
Coating No. Steel sheet n ° Hydrogen duringannealing(%) Annealing temperature (° C) Pto., Decondensation duringannealing (° C) Plate thickness (mm) Al nocoating (%) M1 S1 3 800 1 2 0.39 M2 S2 2 900 5 6 0.45 M3 S3 4 850 10 8 0.37 M4 S4 6 800 15 10 0.41 M5 S5 8 750 20 12 0.46 M6 S6 10 700 25 6 1.18 M7 S7 1 650 30 7 0.34 M8 S8 4 900 40 8 0.63 M9 S9 6 850 50 10 0.38 M10 S10 8 800 1 6 0.47 M11 S11 10 750 5 7 0.36 M12 S12 2 700 10 8 1.14 M13 S13 4 650 15 9 0.49 M14 S14 6 900 20 10 0.37 M15 S15 8 850 25 6 0.31 M16 S16 10 800 30 7 0.35 M17 S17 2 750 40 8 0.33 M18 S18 4 700 50 9 0.44 M19 S19 6 650 1 10 0.38
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Coated Plate Hydrogen Temperature Pto., De Thickness Al no M20 S20 8 900 5 4 0.42 M21 S21 10 850 10 1 0.47 M22 S22 2 800 15 20 0.36 M23 S23 3 900 20 6 0.37 M24 S24 5 850 25 7 0.45 M25 S25 7 800 30 8 0.34 M26 S26 10 750 40 9 0.38 M27 S27 5 700 50 10 0.49 M28 S28 10 650 30 6 0.35 M29 S29 5 750 -20 7 0.36 M30 S24 5 500 -2 8 0.4 M31 S25 5 600 60 9 0.39 M32 S26 5 800 -40 10 0.47 M33 S26 0 850 2 6 0.53 M34 S25 3 920 65 7 0.51 M35 S27 20 800 -20 8 0.44 M36 S30 5 800 -20 9 0.42 M37 S30 20 800 -20 10 0.43
Table 5 (2/3)
Coating No. Steel sheet n ° D(mm) d(mm) Traction test value Evaluation ofresistance tofragility byhydrogen C in the surface layer (mass%) TS(MPa) El(MPa) M1 S1 0.16 0.09 783 13 3 0.028 M2 S2 0.62 0.38 827 15 3 0.043 M3 S3 1.35 0.9 856 18 3 0.053 M4 S4 1.5 1.2 918 20 3 0.063 M5 S5 1.46 1.42 1064 18 3 0.214
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Coating No. Steel sheet n ° D(mm) d(mm) Traction test value Evaluation ofresistance to C in the surface layer (% M6 S6 2.8 1.8 1249 17 4 0.116 M7 S7 5.6 3.6 1580 6 4 0.128 M8 S8 2.5 2.6 805 15 5 0.029 M9 S9 16 4.2 833 24 4 0.041 M10 S10 4.9 5.1 861 27 4 0.052 M11 S11 1.05 1.1 932 25 4 0.070 M12 S12 51 1.4 1027 22 4 0.086 M13 S13 3.5 3.7 1629 6 5 0.114 M14 S14 3.9 4.5 1573 4 5 0.133 M15 S15 1.3 1.5 795 13 4 0.025 M16 S16 2.2 1.6 816 12 5 0.041 M17 S17 2 3.2 988 10 5 0.058 M18 S18 7.2 4.4 1204 8 5 0.064 M19 S19 4.2 3.8 1550 5 5 0.089 M20 S20 3.7 2.8 1591 5 4 0.108 M21 S21 5.2 4.8 1642 6 5 0.130 M22 S22 8.3 8.1 812 25 5 0.028 M23 S23 4.4 4.3 930 22 5 0.045 M24 S24 8.2 6.7 979 22 5 0.057 M25 S25 100 16 1375 7 5 0.066 M26 S26 9.5 12 1561 6 4 0.075 M27 S27 2.2 3.4 1597 5 5 0.110 M28 S28 2.3 2.3 1606 6 5 0.145 M29 S29 - - 978 20 1 - M30 S24 1 0.85 1042 22 1 0.059 M31 S25 20.5 8.5 1359 7 1 0.068 M32 S26 0.51 - 1594 6 1 0.256
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Coated Plate D d Test value Evaluation gives C in layer ment n ° steel n ° (mm) (mm) traction resistance The of surface (% M33 S26 0.02 0.1 1585 6 1 0.238 M34 S25 22.8 6 1408 7 1 0.064 M35 S27 - - 1616 5 1 - M36 S30 0 1.3 453 36 5 0.016 M37 S30 0 - 447 36 5 0.017
Table 5 (3/3)
Coating no. Steel sheet n ° Nano hardness Note inside ofsteel sheet (GPa) layer ofsurface (GPa) layer ofsurface /inland M1 S1 3.95 2.86 0.73 Ex. Inv. M2 S2 4.42 2.87 0.65 Ex. Inv. M3 S3 4.80 2.84 0.59 Ex. Inv. M4 S4 5.85 2.85 0.49 Ex. Inv. M5 S5 9.89 3.00 0.30 Ex. Inv. M6 S6 11.80 3.50 0.30 Ex. Inv. M7 S7 14.10 4.18 0.30 Ex. Inv. M8 S8 4.17 2.87 0.69 Ex. Inv. M9 S9 4.50 2.84 0.63 Ex. Inv. M10 S10 4.88 2.84 0.58 Ex. Inv. M11 S11 6.13 2.93 0.48 Ex. Inv. M12 S12 8.62 3.04 0.35 Ex. Inv. M13 S13 14.30 6.06 0.42 Ex. Inv. M14 S14 13.90 4.50 0.32 Ex. Inv. M15 S15 4.07 2.78 0.68 Ex. Inv. M16 S16 4.29 2.84 0.66 Ex. Inv. M17 S17 7.47 2.99 0.40 Ex. Inv.
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Coated Plate Nano hardness Note M18 S18 11.90 3.03 0.25 Ex. Inv. M19 S19 13.70 5.78 0.42 Ex. Inv. M20 S20 13.80 4.85 0.35 Ex. Inv. M21 S21 14.00 4.77 0.34 Ex. Inv. M22 S22 4.25 2.85 0.67 Ex. Inv. M23 S23 6.09 2.97 0.49 Ex. Inv. M24 S24 7.23 2.97 0.41 Ex. Inv. M25 S25 13.40 3.53 0.26 Ex. Inv. M26 S26 14.20 3.93 0.28 Ex. Inv. M27 S27 13.90 5.14 0.37 Ex. Inv. M28 S28 14.10 6.12 0.43 Ex. Inv. M29 S29 7.21 2.90 0.40 Ex. Comp. M30 S24 9.11 3.03 0.33 Ex. Comp. M31 S25 12.70 3.56 0.28 Ex. Comp. M32 S26 13.80 4.44 0.32 Ex. Comp. M33 S26 13.90 5.29 0.38 Ex. Comp. M34 S25 13.10 3.46 0.26 Ex. Comp. M35 S27 14.30 6.60 0.46 Ex. Comp. M36 S30 2.84 2.65 0.93 Ex. Comp. M37 S30 2.84 2.66 0.94 Ex. Comp.
[00143] In addition, the coated steel sheet was cut in the direction of the thickness, and the hardness of the steel sheet in a cross section was measured by the nano-recess method to a depth of 1/3 of the thickness of the steel sheet. from the coating / ferrite interface. The method of using the nano-indentation method for measurement is according to the first modality.
[00144] The depth d (gm) from the coating / ferrite interface in which the oxide including one or more between Si and Mn was present in the steel was obtained by observing the cross section
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[00145] Resistance to hydrogen embrittlement was assessed as follows: The coated layer was peeled off using a 5% hydrochloric acid solution, a cathodic charge was performed for 24 gardens in a CH3COOHCH3COONa buffer solution having a pH of 4 , 5 at a current density of 2A / dm ² using the steel plate as a cathode and a galvanostat (HAB-151, produced by Hokuto Denko Corporation), subsequently Cd electroplating was performed, the steel plate was cut in a size of 20 mm x 100 mm, and a slit having a depth of 50% of the thickness of the plate was introduced in the central portion in the longitudinal direction, thus producing a specimen. The steel sheet was fractured in a three-point bend test using an Instrom test machine (type number 3380), the fractured surface was observed using a SEM (S-800, produced by Hitachi Ltd.), and the fragile fractured surface area ratio at the observation site was obtained, thus assessing the resistance to hydrogen embrittlement. Ratings of 3 or higher represent excellent resistance to hydrogen embrittlement.
[00146] Classification 1: the area ratio of the fragile fractured surface is greater than 50%.
[00147] Classification 2: the area ratio of the fragile fractured surface is more than 30% to 50%.
[00148] Classification 3: the area ratio of the fragile fractured surface is more than 20% to 30%.
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60/71 [00149] Classification 4: the area ratio of the fragile fractured surface is more than 10% to 20%.
[00150] Classification 5: the area ratio of the fragile fractured surface is 10% or less.
[00151] It is discovered from the results of the evaluation in Table 5 that the coated steel sheet of the modality is excellent in terms of resistance to embrittlement by hydrogen.
(Third embodiment) [00152] Hereinafter, a third embodiment of the present invention will be described in detail. Initially, the components of the steel plate used in the modality are the same as in the second modality, and thus will not be described.
[00153] Next, it will be described why the coated layer used in the modality is limited. The same reason for the limitation that in the second modality will not be described, and only the differences will be described.
[00154] The reason why the range of Al amount in the coated layer is adjusted to 0.01% to 1% is that, when Al amount is less than 0.01%, dominant Zn oxide waste is generated significantly on the surface of the coating bath, and the appearance after coating is degraded. When the amount of Al exceeds 1%, the Fe-Zn bond in the coated layer becomes significantly suppressed, the speed of the continuous coating line is reduced, and productivity is degraded.
[00155] The coated layer used in the modality is the same as the galvanized coated layer of the first modality.
[00156] The reason why the range of thickness D of the soft layer (softened layer) in which the nano hardness generated at that moment is 75% or less than that inside the steel sheet is set to d / 4 <D <2d is that folding properties are more
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61/71 favorable in this range. The detailed reason is not clear, but it is considered that the above fact results from the effect of the oxides present in this range to suppress fracture propagation.
[00157] The method of production of the galvanized steel sheet having the excellent properties of the modality will be described. The same portions as those of the second mode will not be described, and only the difference will be described.
[00158] The composition of the steel sheet, the casting conditions, and the processes through annealing are the same as in the second modality.
[00159] The annealed steel sheet is cooled to a range of 350 ° C to 550 ° C, immersed in an annealing bath from 440 ° C to 480 ° C, removed from the bath, controlled to have a predetermined amount of coating, and subjected to a heating treatment for 10 seconds to 60 seconds at a plate temperature of 400 ° C to 600 ° C, thus diffusing the Fe in the coated layer and forming a bound coated layer containing a predetermined Fe concentration. As bonding conditions, the heat treatment is preferably carried out for 10 seconds to 60 seconds at a plate temperature of 410 ° C to 530 ° C in order to guarantee the quality of the steel sheet, and is preferably carried out for 10 seconds to 40 seconds from the point of view of suppressing the growth of a Γ phase in the coated layer. .
[Example 4] [00160] In the following, an example of the modality will be described, but the conditions of the example are an example of the conditions used to confirm the feasibility and effects of the modality, and the modality is not limited to that example of the conditions, The modality can employ a variety of conditions within the essence of the modality as long as the objective of the modality is
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[00161] Other elements that are not included in Table 6 are not added, and included only a small amount of unavoidable impurities.
[00162] Steel sheets having the steel components and sheet thicknesses shown in Table 6 were subjected to an annealing treatment at the annealing temperatures, hydrogen concentrations, and dew points as shown in Table 7, immersed in a bath coating of molten Zn with a bath temperature of 450 ° C for 3 seconds, removed from the bath, controlled to have an amount adhered to a single surface up to 1 gm to 20 gm by gas drying, reheated to a plate temperature 400 ° C to 600 ° C to diffuse the Fe in the coated layer, and then cooled to room temperature using nitrogen gas. After the coating on the coated steel sheet obtained was dissolved by an acid, the results of the chemical analyzes were as shown in Table 7 as Al (%) in the coating and Fe (%) in the coating.
Table 6
Steel plate no. C in steel (%) Si in steel (%) Mn in steel (%) Epess. of plate t (mm) S1 0.10 0.50 0.01 1.20 S2 0.15 0.005 0.10 1.60 S3 0.20 0.10 0.50 1.80 S4 0.25 0.10 1.00 2.00 S5 0.30 0.50 2.00 2.30 S6 0.40 0.50 3.00 2.70 S7 0.50 0.50 0.01 3.20 S8 0.10 1.00 0.10 1.00 S9 0.15 1.00 0.50 1.60
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Steel plate no. C in steel (%) Si in steel (%) Mn in steel (%) Epess. of plate t (mm) S10 0.20 1.00 1.00 1.80 S11 0.25 2.00 2.00 2.00 S12 0.30 2.00 3.00 2.30 S13 0.40 2.00 0.01 2.70 S14 0.50 0.01 0.10 3.20 S15 0.10 0.10 0.50 1.20 S16 0.15 0.10 1.00 1.60 S17 0.20 0.10 2.00 1.80 S18 0.25 0.50 3.00 2.00 S19 0.30 0.50 0.01 2.30 S20 0.40 0.50 0.10 2.70 S21 0.50 1.00 0.50 3.20 S22 0.10 1.00 1.00 1.20 S23 0.15 1.00 2.00 1.60 S24 0.20 2.00 3.00 1.80 S25 0.25 2.00 0.01 2.00 S26 0.30 2.00 0.10 2.30 S27 0.40 0.01 0.50 2.70 S28 0.50 0.10 1.00 3.20 S29 0.20 1.20 1.50 1.00 S30 0.05 0.10 0.50 1.80
Table 7 (1/3)
Coating n ^a Steel sheet n ° Hydrogen duringannealing(%) Temp. ofannealing(° C) Point ofcondensation duringannealing(° C) Plate thickness (mm) Al atplate(%) Fe on the plate(%) M1 S1 3 800 1 2 0.20 5
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Coated Plate Hydrogen Temp. of Point of Thickness Al at Fe na M2 S2 1 900 5 6 0.25 7 M3 S3 3 850 10 8 0.19 12 M4 S4 5 800 15 10 0.20 10 M5 S5 7 750 20 12 0.25 12 M6 S6 10 700 25 6 1.00 5 M7 S7 1 650 30 7 0.01 15 M8 S8 3 900 40 8 0.50 5 M9 S9 5 850 50 10 0.20 10 M10 S10 7 800 1 6 0.25 11 M11 S11 10 750 5 7 0.19 12 M12 S12 1 700 40 8 1.00 10 M13 S13 3 650 15 9 0.25 12 M14 S14 5 900 20 10 0.19 10 M15 S15 7 850 25 6 0.01 11 M16 S16 10 800 30 7 0.05 12 M17 S17 1 750 40 8 0.20 10 M18 S18 3 700 50 9 0.25 12 M19 S19 5 650 1 10 0.19 10 M20 S20 7 900 5 4 0.20 11 M21 S21 10 850 10 1 0.25 12 M22 S22 1 800 15 20 0.19 10 M23 S23 3 900 20 6 0.20 12 M24 S24 5 850 25 7 0.25 5 M25 S25 7 800 30 8 0.19 7 M26 S26 10 750 40 9 0.20 12 M27 S27 5 700 50 10 0.25 10 M28 S28 10 650 30 6 0.19 11
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Coated Plate Hydrogen Temp. of Point of Thickness Al at Fe na M29 S29 5 750 -20 7 0.18 10 M30 S24 5 500 -2 8 0.20 11 M31 S25 5 600 60 9 0.20 5 M32 S26 5 800 -40 10 0.24 5 M33 S26 0 850 2 6 0.30 0.05 M34 S25 3 920 65 7 0.30 10 M35 S27 20 800 -20 8 0.22 10 M36 S30 5 800 15 9 0.22 10 M37 S30 20 800 -20 10 0.22 10
Table 7 (2/3)
Coatingn ° Platesteel no. D(mm) d(mm) Traction test value C in the surface layer (% inpasta) TS (MPa) El (MPa) M1 S1 0.1 - 783 13 0.028 M2 S2 0.2 - 827 15 0.043 M3 S3 0.4 0.2 856 18 0.053 M4 S4 0.5 0.3 918 20 0.063 M5 S5 0.1 0.025 1064 18 0.214 M6 S6 2.5 1.5 1249 17 0.116 M7 S7 4.5 2.5 1580 6 0.128 M8 S8 2.1 2.2 805 15 0.030 M9 S9 15 3.2 833 24 0.041 M10 S10 4.2 2.4 861 27 0.052 M11 S11 0.2 0.3 932 25 0.070 M12 S12 50 0.4 1027 22 0.087 M13 S13 2.4 2.6 1629 6 0.114 M14 S14 3.8 4.4 1573 4 0.133
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Coatingn ° Platesteel no. D(mm) d(mm) Traction value test of C in the surface layer (% in M15 S15 0.6 0.8 795 13 0.025 M16 S16 1.4 0.8 816 12 0.041 M17 S17 1.2 2.4 988 10 0.058 M18 S18 6.1 3.3 1204 8 0.064 M19 S19 3.2 2.8 1550 5 0.085 M20 S20 3.3 2.4 1591 5 0.108 M21 S21 5.1 4.7 1642 6 0.130 M22 S22 6.3 6.1 812 25 0.028 M23 S23 3.7 3.6 930 22 0.043 M24 S24 7.8 6.3 979 22 0.057 M25 S25 100 15 1375 7 0.066 M26 S26 8.4 11 1561 6 0.075 M27 S27 1.2 2.4 1597 5 0.110 M28 S28 1.6 1.6 1606 6 0.145 M29 S29 - - 978 20 - M30 S24 0.16 0.01 1042 22 0.059 M31 S25 20 8 1359 7 0.068 M32 S26 0.01 - 1594 6 0.256 M33 S26 0.02 0.1 1585 6 0.238 M34 S25 22 5.2 1408 7 0.064 M35 S27 - - 1616 5 - M36 S30 0 0.3 453 36 0.016 M37 S30 0 - 447 36 0.017
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Table 7 (3/3)
Coating No. Steel sheet n ° Nano hardness Classification offolded portion Classif. givescross section of the folded portion Note inlandsteel sheet(GPa) surface layer (GPa) surface / interior layer M1 S1 3.95 2.86 0.72 3 3 Ex. Inv, M2 S2 4.42 2.87 0.65 4 3 Ex. Inv, M3 S3 4.80 2.84 0.59 3 3 Ex. Inv, M4 S4 5.85 2.85 0.49 3 4 Ex. Inv, M5 S5 9.89 3.00 0.30 3 4 Ex. Inv, M6 S6 11.80 3.50 0.30 4 5 Ex. Inv, M7 S7 14.10 4.18 0.30 4 5 Ex. Inv, M8 S8 4.17 2.87 0.69 4 5 Ex. Inv, M9 S9 4.50 2.84 0.63 5 5 Ex. Inv, M10 S10 4.88 2.84 0.58 5 5 Ex. Inv, M11 S11 6.13 2.93 0.48 3 4 Ex. Inv, M12 S12 8.62 3.04 0.35 3 4 Ex. Inv, M13 S13 14.30 6.06 0.42 4 5 Ex. Inv, M14 S14 13.90 4.50 0.32 4 5 Ex. Inv, M15 S15 4.07 2.78 0.68 3 4 Ex. Inv, M16 S16 4.29 2.84 0.66 4 5 Ex. Inv, M17 S17 7.47 2.99 0.40 4 5 Ex. Inv, M18 S18 11.90 3.03 0.25 5 5 Ex. Inv, M19 S19 13.70 5.78 0.42 5 5 Ex. Inv, M20 S20 13.80 4.85 0.35 4 5 Ex. Inv, M21 S21 14.00 4.77 0.34 4 5 Ex. Inv, M22 S22 4.25 2.85 0.67 5 5 Ex. Inv, M23 S23 6.09 2.97 0.49 5 5 Ex. Inv,
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Coated Plate Nano hardness Classified Classif. gives Note M24 S24 7.23 2.97 0.41 5 5 Ex. Inv, M25 S25 13.40 3.53 0.26 5 5 Ex. Inv, M26 S26 14.20 3.93 0.28 5 4 Ex. Inv, M27 S27 13.90 5.14 0.37 5 4 Ex. Inv, M28 S28 14.10 6.12 0.43 5 4 Ex. Inv, M29 S29 7.21 2.90 0.40 1 1 Ex. Comp. M30 S24 9.11 3.03 0.33 1 1 Ex. Comp. M31 S25 12.70 3.56 0.28 1 1 Ex. Inv. M32 S26 13.80 4.44 0.32 1 1 Ex. Comp. M33 S26 13.90 5.29 0.38 1 1 Ex. Comp. M34 S25 13.10 3.46 0.26 1 1 Ex. Comp. M35 S27 14.30 6.60 0.46 1 1 Ex. Comp. M36 S30 2.84 2.65 0.93 5 5 Ex. Comp. M37 S30 2.84 2.66 0.94 5 5 Ex. Comp. [00163] Meanwhile, the thickness d the steel sheet is slightly
reduced by the diffusion of Fe from the steel sheet due to the bonding treatment after coating, but the reduced amount is a maximum of 5 pm, and there is no substantial influence. Therefore, in the present application, the thickness of the original plate before coating is treated to be the same as plate thickness t excluding the coating thickness of the steel plate product.
[00164] In addition, the coated steel sheet was cut in the thickness direction, and the hardness of the steel sheet in a cross section was measured by the nano-recess method to a depth of 1/3 of the thickness of the steel sheet from the coating / ferrite interface. How to use the nano-indentation method to measure is in accordance with the first modality.
[00165] The depth d (pm) from the interface
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69/71 coating / ferrite in which the oxide including one or two between Si and Mn was present in the steel was obtained by observing the cross section of the coated steel sheet using a scanning electron microscope (S-800, produced by Hitachi, Ltd.) and confirming the location in which one or more of the oxides that were identified by an energy dispersion type x-ray spectrogram were present at 100 pm. The results are shown in Table 7. [00166] The bending properties were evaluated as follows: The coated steel sheet was cut to a size of 70 mm x 30 mm in order to produce a sample, and a bending test was performed in V at 30 degrees in which a punch having a V shape that has a width of 30 mm and an angle of 30 degrees was pressed in the center of the 70 mm long side. The angle R of the V-shaped punch was adjusted to be constant, 1.0 mm. After the test, the surface in the folded portion was photographed, fractured portions and robust portions were binarized in the observation of the photo, the area ratios were obtained from all observation sites in the fractured portions, thus evaluating the folding properties. The fractured area ratios obtained were given ratings according to the index below, and ratings of 3 or more were adjusted to have reached the acceptable level.
[00167] In addition, the folded portion was implanted in a resin, and the cross section of the folded portion was observed using an optical microscope, thus observing the progression of the fracture. In the cross-sectional observation, between the observation sites, the depth of the fracture that advanced farther from the surface layer was measured, and the ratio of the depth of the fracture to the thickness of the steel plate was used as the rate of fracture advance. . The rate of progress of the fracture obtained was given a classification according to the following index, and classifications of 3 or
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70/71 higher were adjusted to have reached the acceptable level. The results are shown in Table 7.
[00168][00169][00170]20%. Observation of the surface of the folded portionClassification 1: the fracture area ratio is more than 20%.Classification 2: the fracture area ratio is more than 10% at [00171]10%. Classification 3: the fracture area ratio is more than 5% at [00172]5%. Classification 4: the fracture area ratio is more than 1% at [00173][00174][00175]20%. Classification 5: the fracture area ratio is 1% or less.Observation of the cross section of the folded portionClassification 1: the fracture advance rate is more than [00176] Classification 2: the rate of fracture advance is more than
10% to 20%.
[00177] Classification 3: fracture advance rate is more than
5% to 10%.
[00178] 1% to 5%. Classification 4: the rate of fracture advance is more than [00179] less. Classification 5: fracture advance rate is 1% or [00180] It is found from the evaluation of the results in Table 7 that
the coated steel sheet of the present invention is excellent in terms of folding properties.
Industrial Applicability
[00181] According to the present invention, it is possible to provide
a coated steel sheet that is excellent in terms of resistance to hydrogen embrittlement. In addition, according to the present invention, it becomes possible to produce a steel sheet
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71/71 high strength galvanized and annealed which is excellent in terms of resistance to hydrogen embrittlement without degrading productivity. In particular, the present invention is intended to be used as a reinforcement member for automobiles, and has great industrial significance.
[00182] As described above, according to the present invention, it is possible to provide a coated steel sheet which is excellent in terms of folding properties. In particular, the present invention is intended to be used as a reinforcement member for automobiles, and has great industrial significance.

权利要求:
Claims (3)
[1]
1. Galvanized steel sheet having a tensile strength of 770 MPa or more, characterized by the fact that it comprises:
a steel plate portion containing, in% by mass,
C: 0.05% to 0.50%,
Si: 0.005% to 2.5%,
Mn: 0.01% to 3.0%,
Al: 0% to 0.5%,
Ni: 0% to 2.0%,
Cu: 0% to 2.0%,
Cr: 0% to 2.0%,
Mo: 0% to 2.0%,
B: 0% to 0.002%,
Ti: 0% to 0.1%,
Nb: 0% to 0.1%,
V: 0% to 0.1%,
REM: 0% to 0.1%,
Ca: 0% to 0.1%,
P: limited to 0.03% or less,
S: limited to 0.02% or less,
N: limited to 0.0060% or less, the rest being Fe and the inevitable impurities; and a coated layer formed on the surface of the steel plate portion, wherein the coated layer is a galvanized coated layer or a galvanized and annealed coated layer, the galvanized coated layer containing:
Al: 0.01% to 1.5%, and one or more elements selected from Pb, Sb, Si, Sn,
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[2]
2/3
Mg, Mn, Ni, Cr, Co, Ca, Cu, Li, Ti, Be, Bi, and REM in a total of 0% to 3.5% with a remaining compound of Zn and the inevitable impurities, and the coated layer galvanized and annealed containing:
Fe: 5% to 15%,
Al: 0.01% to 1%, and one or more elements selected from Pb, Sb, Si, Sn, Mg, Mn, Ni, Cr, Co, Ca, Cu, Li, Ti, Be, Bi, and REM in total 0% to 3.5% with the remainder being Zn and the inevitable impurities, the steel plate portion has a soft layer that directly connects the interface with the coated layer and an inner layer that is different from the soft layer, the thickness D of the soft layer is 0.001% to 5% of the thickness t of the sheet steel portion, where the soft layer has a metallographic structure having a ferrite area ratio of 95% or more and an average thickness of 0.01 pm at 10 pm, and when the hardness of the soft layer measured by the nano-indentation method is indicated by H1, and the representative hardness of the steel plate portion measured by the nano-indentation method is indicated by Ha in the cross section that goes along the direction of the thickness of the steel plate portion, H1 is 5% to 75% Ha, and the C concentration in the soft layer is 10% less than 30% C concentration of the entire steel plate portion.
2. Galvanized steel sheet according to claim 1, characterized by the fact that when an oxide including one or two between Si and Mn is present in a portion of the steel sheet surface layer having a depth of d or less from a coating / ferrite interface, the depth d at which the oxide is present and D satisfy d / 4 <D <2d.
[3]
3. Galvanized steel sheet, according to
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3/3 claim 1, characterized by the fact that the steel plate portion also contains more than 0.10% and 0.50% or less of C.

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法律状态:
2016-11-01| B25D| Requested change of name of applicant approved|Owner name: NIPPON STEEL AND SUMITOMO METAL CORPORATION (JP) |

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2018-04-10| B06F| Objections, documents and/or translations needed after an examination request according [chapter 6.6 patent gazette]|

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2018-11-13| B06T| Formal requirements before examination [chapter 6.20 patent gazette]|Free format text: O DEPOSITANTE DEVE RESPONDER A EXIGENCIA FORMULADA NESTE PARECER POR MEIO DO SERVICO DE CODIGO 206 EM ATE 60 (SESSENTA) DIAS, A PARTIR DA DATA DE PUBLICACAO NA RPI, SOB PENA DO ARQUIVAMENTO DO PEDIDO, DE ACORDO COM O ART. 34 DA LPI. |

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2019-04-16| B07A| Application suspended after technical examination (opinion) [chapter 7.1 patent gazette]|

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2019-08-27| B25D| Requested change of name of applicant approved|Owner name: NIPPON STEEL CORPORATION (JP) |

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2019-11-12| B07A| Application suspended after technical examination (opinion) [chapter 7.1 patent gazette]|

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2020-03-10| B09A| Decision: intention to grant [chapter 9.1 patent gazette]|

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2020-05-05| 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 31/08/2010, OBSERVADAS AS CONDICOES LEGAIS. |

优先权:

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申请号 | 申请日 | 专利标题

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JP2009200467|2009-08-31|

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JP2009217578|2009-09-18|

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JP2009216986|2009-09-18|

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PCT/JP2010/064839|WO2011025042A1|2009-08-31|2010-08-31|High-strength hot-dip galvanized steel sheet and process for producing same|

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