HOT LAMINATED STEEL SHEET AND METHOD FOR ITS PRODUCTION

专利摘要:
abstract patent of invention: "hot rolled steel plate and method for its production". a hot-rolled steel sheet is provided in which the composition contains, in% by weight, c: 0.01% to 0.2%; si: 2.5% or less; mn: 4.0% or less; p: 0.10% or less; s: 0.03% or less; al: 0.001% to 2.0%; n: 0.01% or less; o: 0.01% or less; ti: 0.01 to 0.30%; and the balance being composed of iron and impurities and the structure is composed of, in fraction of volume, 90% or more of tempered martensite with an average aspect ratio of 2 or less, or 90% or more in the total of both between martensite temperate and lower bainite.
公开号:BR112015024854B1
申请号:R112015024854-3
申请日:2014-05-13
公开日:2020-03-10
发明作者:Akifumi SAKAKIBARA；Tatsuo Yokoi；Hiroshi Shuto；Yuuki Kanzawa；Masafumi Azuma
申请人:Nippon Steel Corporation；
IPC主号:

专利说明:

Descriptive Report of the Invention Patent for "HOT LAMINATED STEEL SHEET AND METHOD FOR ITS PRODUCTION".
Technical field [001] The present invention relates to a high-strength hot-rolled steel sheet having a maximum tensile strength of 980 MPa or more and excellent toughness at low temperature and a method of producing it, and in particular , refers to a hot-rolled steel sheet including low temperature toughness to allow use in a cryogenic region and a method of producing it.
Background [002] The weight reduction of an automobile chassis was promoted by using a high-strength steel plate to suppress the emission of carbon dioxide gas by an automobile. In addition, in addition to mild steel sheets, several high-strength steel sheets having a maximum tensile strength of 980 MPa or more have been used for car chassis to ensure passenger safety.
[003] In addition, there is a need for such steel plate used for an element to be shaped to then be joined to an automobile as a part and then even if the element receives a shock due to a collision or similar, the element will not is easily destroyed and, in addition, there is also a need to improve toughness at low temperature to ensure shock resistance in a particular cold region. This low-temperature toughness is prescribed by vTrs (Charpy fracture transition temperature) or similar. Therefore, it is also necessary to consider the shock resistance itself of a steel product. In addition, when the steel sheet has its strength increased, the plastic deformation of the steel sheet becomes difficult, while the concern about destruction becomes greater, and therefore toughness is required as an important property.
[004] As for the method of improving toughness in a high strength steel plate, for example, Patent Literature 1 describes a production method, and a method of adjusting a martensite phase with an adjusted aspect ratio is known for a main phase.
[005] It is generally known that the aspect ratio of martensite depends on the aspect ratio of the austenite grains before processing. That is, martensite with a large aspect ratio means martensite transformed from non-recrystallized austenite (austenite extended by lamination), and martensite with a small aspect ratio means martensite transformed from recrystallized austenite.
[006] It is necessary to increase the finishing temperature of the lamination to allow recrystallization of the austenite, and there is a tendency for the grain diameter of the martensite to become large. It is generally known that large diameter refining creates an effect of improving toughness and therefore when the aspect ratio decreases, it is possible to decrease a toughness deterioration factor resulting from the shape, but the resulting toughness deterioration is caused of the hardening of the crystal grains, so that there is a limit of improvement of the tenacity at low temperature.
[007] Patent Document 1 refers to a method for producing a thick steel sheet for a structural element of a large industrial construction machine and the like that includes both high strength and high tenacity by obtaining a ratio of appearance of 3 to 18 of the grains of the previous austenite, but the steel sheet for automobiles must also have excellent tenacity at low temperature. In addition, the steel sheet having grains with such an aspect ratio has anisotropy of mechanical properties, so as to have difficulty in being formed into a general element of automobiles, resulting in the fact that there is a problem that its use is limited.
[008] Patent Literature 2 describes that ferrite grains with an aspect ratio of 2 or less are adjusted to a main phase in order to manufacture a high tenacity steel sheet. However, the main phase of this steel sheet is ferrite, so it is difficult to guarantee the tensile strength of 980 MPa or more.
[009] Patent Literature 3 describes that carbides are made to precipitate finely in ferrite having an average grain diameter adjusted to 5 to 10 pm, in order to improve the low temperature toughness and toughness of a steel plate. According to the method described in Patent Literature 3, solid solutions of Ti and / or the like in steel are made to precipitate as carbides, to thereby increase the strength of the steel sheet. However, to ensure a tensile strength of 980 MPa or more, finer precipitation and denser dispersion are required, and detailed adjustments to the cooling conditions after finishing laminating are required. Therefore, it is conceivable that the steel sheet produced by the method has difficulties in steadily guaranteeing a tensile strength of 980 MPa or more.
[0010] Patent Literature 4 describes that the structure of a steel plate is adjusted to a single phase made of bainite phase or bainitic ferrite phase and the amount of cementite at the edges of the grains is suppressed, thus improving the low toughness steel sheet temperature. However, the steel sheet described in Patent Literature 4 has a tensile strength of 604 to 764 mpA, and therefore it is conceivably difficult to guarantee a tensile strength of 980 MPa or more. In addition, the production of a thick hot-rolled steel sheet having a sheet thickness of 8.7 mm or more is described, but no mention is made of the method of producing a thin hot-rolled steel sheet used for a car's steel plate.
[0011] Patent Literature 5 describes that when producing a high strength steel sheet having a tensile strength of 980 MPa or more, the generation of an MA phase (mixed sea-tensite-austenite structure) to be a point starting point of destruction is suppressed, in order to improve low temperature toughness. Generally, the mechanism in which the MA phase appears results from the fact that C is concentrated in austenite for some type of cause. Thus, the type of steel described in Patent Literature 5 contains fixed amounts of Ti, Nb, V, and Mo, which are carbide-forming elements, in order to capture C to suppress the concentration in austenite, and thus the generation of the MA phase. is suppressed.
[0012] However, these carbide-forming elements are expensive and need to be added in large quantities, so that the steel sheet described in Patent Literature 5 is poor in economic efficiency. Additionally, in Patent Literature 5, the low temperature toughness of a weld joint portion is mentioned, but no mention is made regarding the low temperature toughness of a parent metal, which is important for the steel plate to a car.
[0013] As above, a high strength steel plate that exceeds 980 MPa has difficulties including excellent low temperature toughness simultaneously.
List of citations Patent Literature [0014] Patent Literature 1: Japanese Laid-open Patent Publication No. 2011-52321 [0015] Patent Literature 2: Japanese Laid-open Patent Publication No. 2008-231474 [0016] Patent Literature 3: Japanese Laid-open Patent Publication No. 2011-17044 [0017] Patent Literature 4: Japanese Laid-open Patent Publication No. 2013-014844 [0018] Patent Literature 5: Japanese Laid-open Patent Publication No. 2012- 077340 [0019] Patent Literature 6: Japanese Laid-open Patent Publication No. 2000-109951 [0020] Patent Literature 7: Japanese Laid-open Patent Publication No. 2010-138421 [0021] Patent Literature 8: Japanese Laid- open Patent Publication No. 2009-052106 [0022] Patent Literature 9: Japanese Laid-open Patent Publication No. 2008-266695 [0023] Patent Literature 10: Japanese Laid-open Patent Publication No. 2006-161139 Summary of the invention Problem technical [0024] The present invention was made in consideration that of the problems described above, and its objective is to provide a hot rolled steel sheet having both maximum tensile strength of 980 MPa or more and excellent low temperature toughness and a method for its production.
Solution to the problem [0025] The present inventors were successful in producing a steel sheet having a maximum tensile strength of 980 MPa or more and excellent low temperature toughness by optimizing the components and production conditions of a steel sheet hot rolled and control the structure of the steel cover. Its essence is as follows.
[0026] (1) The hot-rolled steel plate includes: a structure which is a composition containing, in% by mass, [0027] C: 0.01 to 0.2%;
[0028] Si: 2.5% or less (not including "0" (zero));
[0029] Mn: 4.0% or less (not including "0" (zero));
[0030] P: 0.10% or less;
[0031] S: 0.03% or less;
[0032] Al: 0.001% to 2.0%;
[0033] N: 0.01% or less (not including "0" (zero));
[0034] O: 0.01% or less (not including "0" (zero));
[0035] Ti: 0.03 to 0.30%;
[0036] Nb: "0" (zero) at 0.30%;
[0037] Cu: "0" (zero) at 2.0%;
[0038] Ni: "0" (zero) at 2.0%;
[0039] Mo: "0" (zero) at 1.0%;
[0040] V: "0" (zero) at 0.3%;
[0041] Cr: "0" (zero) at 2.0%;
[0042] Mg: "0" (zero) at 0.01%;
[0043] Ca: "0" (zero) at 0.01%;
[0044] REM: "0" (zero) at 0.1%;
[0045] B: "0" (zero) at 0.01%; and [0046] the balance being composed of iron and impurities and in which in fraction of volume, 90% or more of tempered martensite with shaped grain or in fraction of volume, 90% or more in total of both tempered martensite with shaped grain and in volume fraction of lower bainite they are contained and the average aspect ratio of tempered martensite and lower bainite is 2% or less.
[0047] (2) The hot-rolled steel sheet according to item (1) described above, in which the effective diameter of the tempered martensite and lower bainite crystal grain is 10 gm or less.
[0048] (3) The hot-rolled steel plate according to item (1) or (2) described above, in which 1 x 106 (pieces / mm2) or more of iron-based carbides exist in tempered martensite and bottom bainite.
[0049] (4) High-strength hot-rolled steel plate according to any of items (1) to (3), also includes: [0050] in% by weight, [0051] Nb: 0.01 to 0 , 30%.
[0052] (5) The hot-rolled steel plate according to any of the items (1) to (4) described above, also includes: [0053] in mass%, [0054] one element or two or more elements selected the group consisting of [0055] Cu: 0.01 to 2.0%;
[0056] Ni: 0.01 to 2.0%;
[0057] Mo: 0.01 to 1.0%;
[0058] V: 0.01 to 0.3%; and [0059] Cr: 0.01 to 2.0%, [0060] (6) The hot-rolled steel plate according to any of the items (1) to (5) described above, also includes: [0061] in % by mass, [0062] one type or two or more elements selected from the group consisting of [0063] Mg: 0.0005 to 0.01%;
[0064] Ca: 0.0005 to 0.01%; and [0065] REM: 0.0005 to 0.1%.
[0066] (7) The hot-rolled steel plate according to any of the items (1) to (6) described above, also includes: [0067] in mass%, [0068] B: 0.0002 to 0, 01%.
[0069] (8) The hot-rolled steel sheet according to any of the items (1) to (7) described above, in which a galvanized layer or a bonded galvanized layer is included on the surface of the hot-rolled steel sheet.
[0070] (9) A method of producing a hot rolled steel sheet, includes: [0071] melting a steel containing: [0072] in% by mass, [0073] C: 0.01 to 0, 2%;
[0074] Si: 2.5% or less (not including "0" (zero));
[0075] Mn: 4.0% or less (not including "0" (zero));
[0076] P: 0.10% or less;
[0077] S: 0.03% or less;
[0078] Al: 0.001 to 2.0%;
[0079] N: 0.01% or less (not including "0" (zero));
[0080] O: 0.01% or less (not including "0" (zero));
[0081] Ti: 0.03 to 0.30%;
[0082] Nb: "0" (zero) at 0.30%;
[0083] Cu: 2.0% (zero) at 2.0%;
[0084] Ni: "0" (zero) at 2.0%;
[0085] Mo: "0" (zero) at 1.0%;
[0086] V: "0" (zero) at 0.3%;
[0087] Cr: "0" (zero) at 2.0%;
[0088] Mg: 0.01% "0" (zero);
[0089] Ca: "0" (zero) at 0.01%;
[0090] REM: "0" (zero) at 0.1%;
[0091] B: "0" (zero) at 0.01%; and [0092] the balance being composed of iron and impurities and cast the steel in a plate, and then directly heat the cast plate to 1200 ° C or more or cool the cast plate once and then heat the cast plate to 1200 ° C or more; perform hot rolling in which the rolling reduction ratio in the final roughing rolling stage is set to 25% or more and the rolling temperature is set to less than 1100 ° C and the rough rolling is completed, a crude lamination piece obtained is heated to 10 ° C or more prior to roughing lamination, and the finishing temperature of the finishing lamination to be carried out subsequently is adjusted to 900 ° C or more; and perform cooling at an average cooling rate of 50 ° C / s or more from the finish temperature of the finishing laminate to 400 ° C and perform the bend at 100 ° C or more to less than 400 ° C .
[0093] (10) The method of producing the hot-rolled steel sheet according to item (9) described above, also includes: performing a galvanizing treatment or a galvanostegia treatment after winding.
Advantageous effects of the invention [0094] According to the present invention, it is possible to provide a high-strength hot-rolled steel sheet that has a maximum tensile strength of 980 MPa or more and excellent low temperature toughness [0095] Description of embodiments Hereinafter, the contents of the present invention will be explained in detail.
[0096] As a result of an examination determined by the present inventors, it was discovered that, in fraction of volume, 90% or more of tempered martensite of conformed grain having an aspect ratio of the effective crystal grains, (in which the average ratio of aspect will be referred to simply as an aspect ratio, hereinafter), being 2 or less, or 90% or more of the total tempered martensite with shaped grain and lower bainite having an aspect ratio of the effective crystal grains being 2 or less is contained, and also an effective crystal grain diameter of tempered martensite and lower bainite is preferably set to 10 gm or less, and additionally 1 x 106 (pieces / mm2) or more of iron-based carbides that exist in martensite tempered and in the lower bainite are contained, thus making it possible to guarantee a high resistance of 980 MPa or more and a high tenacity at low temperature.
[0097] Here, the effective crystal grain is an area surrounded by a grain border with a disorientation of 15 ° or more and can be measured using an EBSD or similar. Your details will be described later.
[Microstructure of a steel sheet] [0098] Initially, the microstructure of a hot-rolled steel sheet of the present invention will be explained.
[0099] In the hot-rolled steel sheet of the present invention, tempered martensite or a mixed structure of tempered martensite and lower bainite is adjusted for the main phase and its total volume fraction is adjusted to 90% or more, and thus a resistance maximum traction of 980 MPa or more is guaranteed. Therefore, it is necessary to obtain the main phase being tempered martensite or a mixed structure of tempered martensite and lower bainite.
[00100] In the present invention, tempered martensite is the most important microstructure to include resistance, high hardening capacity in cooking, and tenacity at low temperature. The tempered martensite is an aggregation of lattice-shaped crystal grains and contains carbides based on iron having a larger axis of 5 nm or more inside, and also carbides based on iron are several variants, that is, they belong to a plurality of groups of iron-based carbides extended in different directions.
[00101] In the present invention, when the winding temperature is adjusted to 100 ° C or more to less than 400 ° C, when the martensite structure is obtained once and then is tempered at 100 to 600 ° C, the structure of the tempered martensite can be obtained.
[00102] The lower bainite is also an aggregation of crystal grains in the form of a lattice and contains carbides based on iron having a larger axis of 5 nm inside, and also carbides based on iron are unique variants, ie , belong to a group of iron-based carbides extended in one direction. Observing the direction of the carbide extensions, the tempered martensite and the lower bainite can be easily distinguished. Here, the group of carbides based on iron extended in one direction means a group of carbides based on iron where the difference in the direction of the extension is within 5 °.
[00103] The bottom bainite can be obtained by adjusting the winding temperature between 400 ° and the martensitic transformation point, and as the winding temperature is higher in this temperature range, or as the winding rate is later more slow, the ratio of the lower bainite becomes greater.
[00104] When the volume fraction of one or the total of the tempered martensite and the lower bainite is less than 90%, the maximum tensile strength of 980 MPa or more cannot be guaranteed, resulting in the fact that the maximum resistance to moth of 980 MPa or more, which is the requirement of the present invention, cannot be guaranteed. Therefore, the lower limit of the volume fraction is 90%. However, even if the volume fraction is set to 100%, the strength and excellent low temperature toughness, which are the effects of the present invention, are exhibited.
[00105] Like other structures, by the volume fraction of 10% or less in the total of one type or two or more types between ferrite, new martensite, upper bainite, perlite and retained austenite can also be contained in the structure of the plate. steel.
[00106] Here, new martensite is defined as martensite containing no carbides. The new martensite is highly strong, but it is extremely hard, so the deformation focuses on an interface with a different structure to be liable to become a starting point of destruction, resulting in the fact that the new martensite is poor in toughness. at low temperature. In addition, even if the new martensite is set for the main phase, the hardness varies greatly even in the same new martensite phases, and thus an interface is likely to become a starting point of destruction. Therefore, it is necessary to limit the volume fraction of the new martensite to 10% or less.
[00107] Retained austenite is, when the steel product is plastically deformed at the time of pressing molding or an automobile part is plastically deformed at the time of the collision, transformed into new martensite, thus causing the adverse effect described above similar to the new martensite. Therefore, it is necessary to limit the volume fraction to 10% or less.
[00108] The upper bainite is an aggregation of crystal grains in the form of a lattice and is an aggregation of lattices containing carbides between them. The carbides contained between the trusses become a starting point of destruction, thus reducing the toughness at low temperature. In addition, when compared to the lower bainite, the upper bainite is formed at high temperatures so as to be low in strength, and when the upper bainite is formed excessively, it becomes difficult to guarantee the maximum tensile strength of 980 MPa or more. Such a trend becomes prominent when the volume fraction of upper bainite becomes greater than 10%, so it is necessary to limit the volume fraction to 10% or less.
[00109] Ferrite is a mass of crystal grains and means a structure that does not contain a substructure such as a lattice within itself. Ferrite is the softest structure and causes a decrease in strength, and therefore, to ensure maximum tensile strength of 980 MPa or more, ferrite needs to be limited to 10% or less. In addition, it is extremely soft compared to the tempered sea-tensite or the lower bainite being the main phase, and thus the deformation is concentrated at the interface between both structures to be able to become a starting point of destruction, resulting in fact that low temperature toughness is decreased. Such a trend becomes prominent when the volume fraction becomes greater than 10% so that it is necessary to limit the volume fraction to 10% or less.
[00110] As for tempered martensite, new martensite, bainite, ferrita, perlite, austenite, and the remaining structure that constitutes the steel sheet structure of the present invention as above, identification of these structures, confirmation of existing positions, measurement of area ratios can be performed by the following methods. That is, with a nital reagent and a reagent described in Japanese Laid-open Patent Publication No. 59-219473, of the steel plate, the cross section in the rolling direction or the cross section in the direction perpendicular to the rolling direction is corroded to be observed by a scanning electron microscope and a transmission electron microscope at a magnification of 1000 to 100000 times, and thus the identification of these structures, the confirmation of existing positions, and the measurement of area ratios can be performed.
[00111] In addition, the structures can also be distinguished by analyzing the crystal orientation using a FESEM-EBSD method [crystal orientation analysis method using EBSD: Electron Back-Scatter Diffraction belonging to a scanning microscope field emission electronics (FE-SEM: field emission scanning electron microscope)], or measurement of hardness in micro-regions such as Vickers hardness micro-measurement. Since, for example, the tempered martensite, the upper bainite, and the lower bainite are different in place of formation of the iron-based carbide and matters relating to the crystal orientation (direction of extension) as described above, the bainite and tempered martensite can be easily distinguished by looking at the iron-based carbides inside the lattice-shaped crystal grains using an FE-SEM to examine their extension directions.
[00112] In the present invention, the volume fraction of each of ferrite, perlite, bainite, tempered martensite, and new martensite is calculated by the following method. Initially, a sample is taken from an observation surface that is a cross section in the direction of thickness parallel to the rolling direction of the steel sheet, and the observation surface is polished and etched with nital. Then, the range of 1/8 of the thickness to 3/8 of the thickness with 1Λ of the thickness of the plate being the center is observed by an FE-SEM, and fractions of area are measured, which are adjusted as fractions of volume. In addition, 10 visual fields are each measured at a magnification of 5000 times, and the average value of the measurements is adjusted as an area ratio.
[00113] New martensite and retained austenite are not sufficiently corroded by nital caustication, so that they can be clearly distinguished from the structures described above (ferrite, bainite ferrita, bainite, and tempered martensite) during observation by FE-SEM. Therefore, as a volume fraction of new martensite, the difference between the area fraction of an uncorroded area observed by FE-SEM and the fraction of area of retained austenite measured by X-rays can be obtained.
[00114] Next, the average diameter of the crystal grain and a technique for identifying the structures will be described. In the present invention, the average diameter of the crystal grain, the ferrite, and also the retained austenite are defined using an EBSP-OIM method (Electron Back Scatter Diffraction Pattern-Orientation Image Microscopy). In the EBSP-OIM method, equipment and software are constituted in which a highly inclined sample is irradiated with electron rays in a scanning electron microscope (SEM), a Kikuchi pattern formed by backscattering is photographed by a highly sensitive camera and the image is processed by a computer, and so the crystal orientation at an irradiation point is measured for a short period of time. In the EBSP-OIM method, a microstructure and the crystal orientation of the surface of a sample can be analyzed quantitatively. In addition, the area of analysis of the EBSP-OIM method is an area capable of being observed by an SEM, and the EBSP-OIM method makes it possible to analyze the area with a minimum resolution of 20 nm, which varies depending on the resolution of the SEM. In the present invention, by an image mapped with a disorientation of the crystal grains defined as 15 ° with the minimum value of a high angle grain border generally recognized as a crystal grain border, the grains are visualized, through which it is obtained the average diameter of the crystal grains.
[00115] When the aspect ratio of the effective crystal grains, (each of which means an area surrounded by a grain border with 15 ° or more, here), of the tempered martensite with conformed grain and lower bainite exceeds 2, one excellent toughness cannot be achieved. Therefore, the aspect ratio of the effective crystal grains of tempered martensite and bainite needs to be adjusted to 2 or less.
[00116] Grains made flat in a specific direction have large anisotropy and a fracture spreads along the grain edge during the Charpy test so that the toughness value often becomes low. Thus, effective crystal grains need to be grains that are as equiaxial as possible. In the present invention, the cross section in the direction of the rolling of the steel sheet is observed, and the ratio of the length in the rolling direction (L) to the length in the direction of the sheet thickness (T) (= L / T) is defined as the aspect ratio.
[00117] In the present invention, the sample is taken from an observation surface that is a cross section in the direction of thickness in parallel with the rolling direction of the steel sheet, the observation surface is electropolished, the range of 1/8 of the thickness up to 3/8 of the thickness with 1/4 of the thickness being the center is analyzed by an EBSP-OIM method, the aspect ratios of all the effective grains within a visual field are measured, and an average value of the ratios of aspect is brought up.
[00118] To also improve the tenacity at low temperature, the diameter of the effective crystal grain is desirably adjusted to 10gm or less, in addition to the condition that the tempered martensite or the lower bainite is adjusted for the main phase. The effect of improving low temperature toughness becomes prominent when the average diameter of the effective crystal grain is set to 10 gm or less, so that the diameter of the effective crystal grain is set to 10 gm or less. It is most desirably 8 gm or less. The effective crystal grain diameter to be described here means an area surrounded by the edge of a grain with a crystal disorientation of 15 ° or more to be described by the following technique, and corresponds to a block grain diameter in terms of martensite and lower bai-nita. The lower limit of the lower bainite is desirably set to 5%, also desirably set to 9%, and also desirably set to 12%. In this case, the value of a fracture transition temperature (vTrs) of a Charpy test to be performed in accordance with JIS Z 2242 is likely to be 50 ° C or less.
[00119] Furthermore, the tempered martensite and the lower bainite in the present invention desirably contain 1 x 106 (parts / mm2) or more of iron-based carbides. This is to increase the toughness at low temperature of a source phase to obtain an excellent balance of strength and toughness at low temperature. That is, the quickly cooled sea-tensite is excellent in strength, but poor in toughness, so an improvement in toughness is required. Thus, by making 1 x 106 (pieces / mm2) or more of iron-based carbides precipitate, the toughness of the main phase can also be improved.
[00120] As a result of the present inventors examining the relationship between low temperature toughness and the numerical density of iron-based carbides, it became clear that the adjustment of the numerical density of iron-based carbides within the tempered tensile and the lower bainite to 1 x 106 (pieces / mm2) or more makes it possible to guarantee excellent toughness at low temperature. Therefore, the iron-based carbide is desirably adjusted to 1 x 106 (parts / mm2) or more. It is most desirably 5 x 106 (pieces / mm2) or more, and is also desirably 1 x 107 (pieces / mm2) or more.
[00121] In addition, the iron-based carbides that precipitated by the treatments of the present invention have a size of 300 nm or less, which is small, and most of them precipitated on trusses of martensite and bainite, from which it is deduced that they do not deteriorate toughness at low temperature.
[00122] As a method of measuring the numerical density of the iron-based carbide, a sample is initially taken from an observation surface that is a cross section in the direction of thickness in parallel with the rolling direction of the steel plate. Then, the sample observation surface is polished and etched with nital, and the range of 1/8 of the thickness up to 3/8 of the thickness with 1/4 of the thickness of the plate being the center is observed by an FE-SEM, for thus measuring the numerical density of iron-based carbides. At that time, 10 visual fields are measured each at a magnification of 5000 times, to measure the numerical density of iron-based carbides.
[Chemical composition of the steel sheet] [00123] Next, we will explain the reasons for limiting a chemical composition of the hot rolling of the steel sheet of the present invention. Incidentally, the% of each content means% by mass. [00124] (C: 0.01% to 0.2%) [00125] C is an element that contributes to the increase in the resistance of a base metal and an improvement in the hardening capacity in cooking, but it is also an element that generates iron-based carbides such as cementite (Fe3C) to be the starting point for fractures during hole expansion. When the C content is less than 0.01%, the effect of improving the strength due to the reinforcement of the structure by a low temperature transformation generating phase cannot be obtained. In addition, when the C content exceeds 0.2%, the ductility of the steel sheet decreases, the iron-based carbide such as cementite (Fe3C) to be a starting point for fractures of a secondary shear surface during drilling increases, and forming capacity such as hole expansion capacity deteriorates. Therefore, the C content is adjusted to be in the range of 0.01% to 0.2%.
[00126] (Si: 2.5% or less (not including "0" (zero)) Si is an element that contributes to increase the strength of a base metal and can also be used as a deoxidizing material for molten steel, so that it is preferably contained in a range of 0.001% or more as needed, however, even when an amount greater than 2.5% of Si is contained, the effect of contributing to the increase in resistance is saturated, so that the Si content is adjusted to be in the range of 2.5% or less. In addition, containing 0.1% or more of Si suppresses the precipitation of iron-based carbides such as cementite in the material structure and contributes to improvements in bore strength and expansion capacity due to the increase in its content. In addition, when the Si content exceeds 2.5%, the effect of suppressing the precipitation of iron-based carbides is saturated. Si content is 0.1 to 2.5%. [00127] (Mn: 4.0% or less (not including "0" (zero)) [00128] Mn is contained so that the tempered martensite or the lower bainite can and make the main phase in the structure of the steel plate by reinforcing the solid solution and also by strengthening the rapid cooling. Even when the Mn content is adjusted to greater than 4%, this effect is saturated. On the other hand, when the Mn content is less than 1%, the effect of suppressing the transformation of ferrite and the transformation of bainite during cooling is not easily exhibited, so that 1% or more is desirably contained. It desirably stands at 1.4 to 3.0%.
[00129] (Ti: 0.03 to 0.30%) [00130] Ti is the most important element to allow both excellent low temperature toughness and high resistance of 980 MPa or more to be achieved. P Ti carbonitride or the Ti solid solution delays grain growth during hot rolling, which makes it possible to fine-tune the grain diameter of the hot rolled steel sheet and contributes to an improvement in low temperature toughness. In addition, Ti, in addition to a grain growth property by the solid solution of N, exists as TiN, thus contributing to an improvement in toughness at low temperature while thinning the diameter of the crystal grain when heating the plate . In addition, Ti precipitates as a carbonitride during roughing lamination, thereby thinning the crystal grains and contributing to an improvement in toughness at low temperature, so Ti is particularly important.
[00131] It is necessary to contain 0.03% or more of Ti to obtain 10 pm or less of grain diameter of the hot rolled steel sheet. In addition, even when the Ti content exceeds 0.30%, the effect described above is saturated and economic efficiency deteriorates. The desirable range of Ti content is 0.04 to 0.25%, and is most desirably 0.05 to 0.20%.
[00132] (P: 0.10% or less) [00133] P is an element contained in a cast iron, secretes at the edges of the grains, and decreases the tenacity at low temperature as its content increases. Therefore, it is more desirable for the P content to be lower, and when more than 0.10% is contained, the workability and welding capacity are adversely affected, so that, in particular, the P content is desirably 0.03% or less.
[00134] (S: 0.03% or less) [00135] S is an element contained in molten steel, and when the S content is very large, fracture during hot rolling is caused and also inclusions such as MnS that deteriorate the hole expansion capacity are generated. Therefore, the Si content should be decreased as much as possible, but 0.03% or less is a tolerable range, so the S content is adjusted to 0.03% or less. However, when a certain degree of bore expansion capacity is required, the S content is desirably 0.01% or less, and more desirably 0.005% or less.
[00136] (Al: 0.001 to 2.0%) [00137] Al suppresses the formation of crude cementite and improves toughness at low temperature. In addition, Al can be used as a deoxidizing material. However, containing Al excessively increases the number of crude inclusions based on Al to cause deterioration of the hole expansion capacity and surface flaws. Therefore, the upper limit of the Al content is adjusted to 2.0%. The upper limit of the Al content is desirably 1.5%. Incidentally, adjusting the Al content to less than 0.001% is difficult, and so this is the substantial lower limit.
[00138] (N: 0.01% or less (not including "0" (zero)) [00139] N exists as TiN, thus contributing to an improvement in toughness at low temperature while thinning the diameter of the crystal grain at the time of heating the plate. However, there is a concern that N forms a gas bubble during welding to decrease the resistance of a joint in a welding zone, so it is necessary to adjust the N content to 0.01 On the other hand, adjusting the N content to less than 0.0005% is not economically desirable so that the N content is desirably adjusted to 0.0005% or more.
[00140] (O: 0.01% or less (not including "0" (zero)) [00141] O forms oxides to deteriorate the forming capacity, so its content needs to be suppressed. When the O content exceeds 0.01% in particular, this trend becomes prominent, so it is necessary to adjust the O content to 0.01% or less. On the other hand, adjusting the O content to less than 0.001% is not economically preferable, so that the O content is desirably adjusted to 0.001% or more.
[00142] The basic chemical composition of the hot rolled steel sheet of the present invention is described above, and also the following components can be contained.
[00143] Nb may also be contained because the Nb carbonitride or the solid Nb solution delays the growth of the grain during hot rolling to thereby be able to fine-tune the grain diameter of the hot rolled steel sheet and improve the low temperature toughness. However, when the Nb content is less than 0.01%, the effect described above cannot be achieved sufficiently. In addition, when the Nb content exceeds 0.30%, the re-crystallization temperature drops significantly, obtaining an aspect ratio of 2 or less of the tempered martensite or lower bainite grains becomes difficult, and low toughness temperature deteriorates. Therefore, when Nb is contained according to need, the Nb content is desirably adjusted to 0.01% to 0.30%.
[00144] (One element or two or more elements selected from the group consisting of Cu, Ni, Mo, V, and Cr) [00145] Cu, Ni, Mo, V, and Cr suppress the transformation of ferrite during cooling and do the steel sheet structure becomes a tempered martensite or lower bainite structure, so that one element or two or more elements selected from the group consisting of these elements, each having the effect of improving the strength of the hot-rolled steel sheet by reinforcement of precipitation or reinforcement of the solid solution, and an element or two or more elements thereof, may also be contained. However, when the content of each of the elements between Cu, Ni, Mo, V, and Cr is less than 0.01%, the effects described above cannot be sufficiently achieved. Furthermore, even when the Cu content is greater than 2.0%, the Ni content is greater than 2.0%, the Mo content is greater than 1.0%, the V content is greater than 0, 3%, and the Cr content is greater than 2.0%, the effects described above are saturated and economic efficiency deteriorates. Thus, when Cu, Ni, Mo, V, and Cr are contained according to need, it is desirable that the Cu content is 0.01% to 2.0%, the Ni content is 0.01% to 2.0 %, the Mo content is 0.01% to 1.0%, the V content is 0.01% to 0.3%, and the Cr content is 0.01% to 2.0%.
[00146] (One element or two or more elements selected from the group consisting of Mg, Ca, and REM) [00147] Mg, Ca, and REM (rare earth element) are elements that control the shape of non-metallic inclusions to be a starting point of destruction by causing deterioration of work capacity and improving work capacity, so that one element or two or more of these elements can also be contained. When the content of each between Mg, Ca and REM is 0.0005% or more, the effect becomes prominent, so that 0.0005% or more of each element between Mg, Ca, and REM is designed to be contained . In addition, even when the Mg content is adjusted to be greater than 0.01%, the Ca content is adjusted to be greater than 0.01%, and the REM content is adjusted to be greater than 0.1% , the effect described above is saturated and economic efficiency deteriorates. Thus, it is desirable that the Mg content be adjusted to 0.0005% to 0.01%, the Ca content to be adjusted to 0.0005% to 0.01%, and the REM content to be adjusted to 0.0005 % to 0.1%.
[00148] (B: 0.0002 to 0.01%) [00149] B delays the transformation of ferrite, thus contributing to make the steel sheet structure become a tempered sea-tensile structure, or lower bainite. Additionally, similarly to C, B segregates at the grain edges and increases the resistance of the grain edges, so as to improve toughness at low temperature, therefore, B may also be contained in the hot-rolled steel sheet. However, adjusting p B content to 0.0002% or more makes this effect prominent, so that the lower limit is desirably adjusted to 0.0002%. On the other hand, when the B content exceeds 0.01%, the effect is saturated and economic efficiency also deteriorates, so that the upper limit is desirably 0.01%. It is most desirably 0.0005 to 0.005%, and also desirably 0.0007 to 0.0030%.
[00150] The above elements are contained in the hot-rolled steel plate and the balance is composed of iron and impurities. Here, like impurities, those contained in raw materials such as ore and scrap are cited as examples, and those to be contained during the production process.
[00151] Incidentally, in relation to other elements, it is confirmed that the effects of the present invention are not impaired even when 1% or less in total of one or two or more elements selected from the group consisting of Zr, Sn, Co, Zn, and W are contained. Among these elements, Sn has a risk that a failure occurs during hot rolling, so that the Sn content is more desirably 0.05% or less.
[00152] On the surface of the hot-rolled steel sheet explained above, a hot-dip galvanized layer is provided by a hot-dip galvanizing treatment, and also a bonded galvanized layer is provided by a bonding treatment after galvanizing , and thus the corrosion resistance can be improved in the hot rolled steel sheet of the present invention having the structures and composition described above. In addition, the galvanized layer is not limited to pure zinc, and may also contain elements such as Si, Mg, Zn, Al, Fe, Mn, Ca, Zr, and the like to achieve another improvement in corrosion resistance. Even when such a galvanized layer is provided, excellent baking hardness and low temperature toughness of the present invention are not impaired.
[00153] In addition, even when any of the treated surface layers made from the formation of organic coating film, laminating film, treatment with organic salts / inorganic salts, treatment without chromium, etc., the effects of the present invention can be obtained.
[00154] [Method of production of steel sheets] [00155] In the following the method of production of the hot-rolled steel sheet of the present invention will be explained.
[00156] A single tempered martensite having the aspect ratio of effective crystal grains being 2 or less, or the total of both between tempered martensite and lower bainite is adjusted to 90% or more to achieve excellent low temperature toughness, or the total of both between tempered martensite and lower bainite is adjusted to 90% or more to achieve excellent toughness at low temperature. In addition, it is desirable that the tempered martensite (and the bottom bainite) have an effective crystal grain diameter of 10 gm or less, and contain 1 x 106 (pieces / mm2) or more of iron-based carbides, and details production conditions to satisfy these conditions will be described below.
[00157] A production method before hot rolling is not particularly limited. That is, what is needed is to adjust the composition to be the composition described above by performing the melting in a blast furnace, an electric oven, etc., and then to run several secondary refineries and then perform the casting by a method such as normal continuous casting, or thin plate casting. During these times, a scrap can also be used as a raw material as long as it can be controlled within the range of components of the present invention.
[00158] A cast plate is heated to a predetermined temperature when hot rolling is performed. in the case of continuous casting, hot rolling can be performed after the casting plate is cooled once to a low temperature, and then reheated, or the hot rolling can also be performed by heating the casting plate without cooling it in particular subsequent to continuous casting.
[00159] The heating temperature of the hot rolling plate needs to be adjusted to 1200 ° C or more. In the hot-rolled steel plate of the present invention, the hardening of the austenite grains is suppressed using the solid solution of Ti (and also Nb desirably), and therefore it is necessary to re-melt the TiC (and also the NbC) that is precipitated at the time of casting. When the heating temperature is less than 1200 ° C, it takes a long time for the Tio and Nb carbides to melt, and therefore the refining of the crystal grain diameter afterwards and the effect of improving the low temperature toughness obtained with it do not occur. Therefore, it is necessary to adjust the heating temperature of the plate to 1200 ° C or more. Furthermore, even if the upper limit of the heating temperature of the plate is not particularly determined, the effects of the present invention are exhibited, but it is not economically preferable to adjust the heating temperature to an excessively high temperature. Therefore, the heating temperature of the plate is desirably adjusted to less than 1300 ° C.
[00160] Roughing lamination must be carried out in which, in the final step, the reduction is carried out at a reduction rate of 25% or more, the lamination temperature in the final step is adjusted to less than 1100 ° C, and the roughing lamination is completed. When the temperature in the final step of the roughing lamination is 1100 ° C or more, the growth rate of the austenite grains increases from the roughing lamination to the finishing lamination and the grain diameter becomes gross, resulting in the fact that that it becomes difficult to guarantee excellent toughness at low temperature. In addition, when the lamination temperature in the final stage is less than 1100 ° C and the reduction ratio in the final stage is adjusted to 25% or more, a more excellent low temperature toughness can be guaranteed.
[00161] This mechanism is unclear, but it is conceivable that due to the generation of Ti carbonitrides caused by stress-induced precipitation, the growth of austenite grains from the roughing lamination to the finishing lamination can be suppressed, and therefore a excellent tenacity at low temperature can be obtained by the effect of making the diameter of fine grain. In addition, this effect becomes prominent as the reduction reduction is greater, but when the reduction ratio is 40% or more, there is a possibility that a scale indentation failure occurs on the steel sheet surface. Consequently, the reduction ratio in the final step of the roughing lamination is desirably adjusted to less than 40%.
[00162] Therefore, the lamination in the final step needs to be carried out at a reduction rate of 25% or more and at a mining temperature of less than 1100 ° C during roughing lamination. It is desirable that the reduction ratio is 25% or more to less than 40% and the lamination temperature is 1000 ° C or more to less than 1100 ° C.
[00163] It is necessary to carry out the heating by a heating equipment so that the temperature increases by 10 ° C or more from the temperature immediately before heating at the time when the finishing lamination starts after the end of the roughing lamination. Heating at 10 ° C or more allows the aspect ratio of tempered martensite or both, tempered martensite and lower bainite to become 2 or less. Such heating can be performed by induction heating equipment, for example, but is not limited to this, and even when heating is performed using a heat holding furnace, energizing heating equipment, and / or similar, this effect can be displayed. In addition, as the time until the finishing lamination begins after the end of the roughing lamination is longer, the heating temperature needs to be increased, so that the time until the finishing lamination begins after the end of the roughing lamination is desirably desired. set to 60 seconds or less. In addition, the time until the finishing lamination begins after the roughing lamination is finished is desirably 30 seconds or less.
[00164] The mechanism why this heating causes the aspect ratio to become 2 or less is not clear, but it is conceivable that the recrystallization progressed by the heating and the recrystallization is completed before the finishing lamination and therefore the aspect ratio of austenite decreases and the aspect ratio of tempered martensite or lower bainite becomes 2 or less.
[00165] The temperature of the finishing lamination (finishing temperature of the finishing lamination) after the roughing lamination is adjusted to 900 ° C or more. In the hot-rolled steel sheet of the present invention, Ti (and also Nb desirably) are contained in large quantities to refine the austenite grain diameter. As a result, when the finishing laminate is finished in a temperature zone of less than 900 ° C, the austenite is not easily recrystallized and the grains are extended in the lamination direction to be liable to cause deterioration in toughness. Thus, the temperature of the finishing laminate is adjusted to 900 ° C or more. It is desirably not less than 90 ° C or greater than 1040 ° C.
[00166] After finishing lamination, cooling is performed at an average cooling rate of 50 ° C / s or more from the temperature of the finishing laminate to 400 ° C and winding is performed. When this average cooling rate is less than 50 ° C / s, ferrite is formed during cooling, resulting in the fact that it is difficult to obtain, in a fraction of volume, 90% or more of the single tempered martensite phase or the total of the tempered martensite and lower bainite as the main phase. Therefore, it is necessary to adjust the average cooling rate to 50 ° C / s or more. However, However, since the ferrite is not formed in a cooling process, air cooling can also be carried out in a temperature zone during the cooling process.
[00167] However, the average cooling rate from Bs to a lower bainite generation temperature is desirably adjusted to 50 ° C / s or more. This is to prevent the formation of upper bainite. When the average cooling rate from Bs to the lower bainite generation temperature is less than 50 ° C / s, the upper bainite is formed, and there is the case where new martensite (martensite whose displacement density is high) is formed between the trusses of bainite, or retained austenite (to be the martensite whose displacement density is high during work) exists, and therefore the ability to harden in cooking and the tenacity at low temperature deteriorate. Note that point Bs is the start temperature of the upper bait generation, which is determined by the components, and is adjusted to 550 ° C for convenience. In addition, the lower bainite generation temperature is also determined by the components, and is adjusted to 400 ° C for convenience. The average rate of cooling is adjusted to 50 ° C / s or more from the temperature of the finishing laminate to 400 ° C, particularly from 550 to 400 ° C, and the average rate of cooling from the end temperature of the laminate up to 400 ° C is set to 50 ° C / s or more.
[00168] Note that adjusting the average cooling rate from the end temperature of the lamination to 400 ° C to 50 ° C / s or more also includes the condition that, for example, the average rate of cooling from the end temperature of lamination up to 550 ° C is set to 50 ° C / s or more and the average cooling rate from 550 to 400 ° C is set to less than 50 ° C / s. However, there is sometimes a case where the upper bainite is likely to be generated under this condition and greater than more than 10% of the upper bainite is partially generated. Therefore, the average cooling rate of 550 to 400 ° C is desirably 50 ° C / s or more.
[00169] The maximum cooling rate below 400 ° C is desirably adjusted to less than 50 ° C / s. This is to allow the structure in which the tempered martensite or the lower bainite with displacement density and the numerical density of the iron-based carbide to be within the ranges described above is the main phase. When the maximum cooling rate is 50 ° C / s or more, it is not possible to cause the iron-based carbide and displacement density to fall within the ranges described above, resulting in the fact that a high hardening capacity in cooking does not can be obtained. Therefore, the maximum cooling rate is desirably set to less than 50 ° C / s. Here, cooling at the maximum cooling rate of less than 50 ° C / s to less than 400 ° C is achieved, for example, by air cooling. In addition, the above cooling not only means cooling, but also includes isothermal retention, that is, coiling to less than 400 ° C. Furthermore, the control of the cooling rate in this temperature zone aims to control the displacement density and the numerical density of the iron-based carbide in the steel plate structure, so that even when cooling is performed once to the temperature of the start of the martensitic transformation (point Ms) or less and then the temperature is increased to perform the reheating , maximum tensile strength of 980 MPa or more, high hardening capacity in cooking, and low temperature toughness, which are the effects of the present invention, can be obtained.
[00170] The winding temperature is adjusted to 100 ° C or more to less than 400 ° C. This is to allow the structure in which the single phase tempered martensite or the tempered martensite and the lower bainite with numerical density of iron-based carbide being within the range described above are the main phase. When the winding temperature is 400 ° C or more, it is not possible to make the single tempered martensite or the tempered martensite and the lower bainite to become the main phase. In addition, when the combining temperature is less than 100 ° C, it is not possible to make the iron-based carbide fall within the range described above, resulting in the fact that excellent toughness cannot be achieved. Therefore, it is necessary to adjust the winding temperature to 100 ° C or more to less than 400 ° C.
[00171] Here, the winding is carried out at a winding temperature being in a range of 400 ° C until the martensite transformation point, in order to generate the lower bainite, and as the temperature is higher in this temperature range or the rate of subsequent cooling is slower, the ratio of bainite becomes greater. On the other hand, when the winding is carried out at a winding temperature that is in the temperature range of the martensitic transformation point up to 100 ° C, the single tempered martensite phase is obtained.
[00172] Incidentally, the winding in this temperature zone aims to control the numerical density of the iron-based carbides in the steel plate structure, so that even when the cooling is carried out once to less than 100 ° C and then to temperature is increased to perform the reheating, the maximum tensile strength of 980 MPa or more and the excellent toughness, which are the effects of the present invention, can be obtained. [00173] In general, to obtain martensite, the transformation of ferrite needs to be suppressed, and cooling to 50 ° C / s or more is necessary. In addition, at low temperature, the temperature zone transitions from the temperature zone whose heat transfer coefficient is relatively low and where it is not easily cooled, called the film boiling region, to the temperature zone whose heat transfer coefficient heat is great and where it is easily cooled, called the boiling temperature region of the nucleate. Therefore, when a temperature zone of less than 400 ° C is set as the cooling stop temperature, the coil temperature fluctuates easily, and with fluctuation, the quality of the material also changes. Therefore, there has often been a case where the normal winding temperature is set to more than 400 ° C or the foot winding performed at room temperature.
[00174] As a result, it is deduced that it was conventionally difficult to discover that the maximum tensile strength of 980 MPa or more and excellent low temperature toughness can be guaranteed simultaneously by winding from 100 to less than 400 ° C as in the present invention.
[00175] Incidentally, it is desirable to perform skin pass lamination at a reduction rate of 0.1% to 2% after all processes have ended with the purpose of correcting the shape of the steel sheet and achieving an improvement in ductility by introducing mobile displacement. In addition, after all the processes are finished, stripping can be carried out on the obtained hot-rolled steel sheet as needed to remove scalings attached to the surfaces of the obtained hot-rolled steel sheet. In addition, it is also possible to perform skin pass lamination or cold lamination at a reduction rate of 10% or less on or off the line on the hot-rolled steel sheet obtained after blasting.
[00176] The steel sheet of the present invention is produced by performing continuous casting, roughing rolling, and finishing rolling which is the normal hot rolling process, as long as the production conditions prescribed above are met, the other conditions production processes are carried out under normal conditions, thus making it possible to guarantee the maximum tensile strength of 980 MPa or more and low temperature toughness, which are the effects of the present invention.
[00177] Furthermore, even if a heat treatment is carried out in a temperature range of 100 to 600 ° C on or off the line for the purpose of carbide precipitation after the hot rolled steel sheet is produced, it is possible to guarantee excellent low temperature toughness and maximum tensile strength of 980 MPa or more which are the effects of the present invention.
[00178] Incidentally, the steel sheet with the maximum tensile strength of 980 Mpa or more in the present invention indicates a steel sheet whose maximum stress stress measured by a tensile test performed in accordance with JIS Z 2241 using a JIS No. 5 specimen cut in a vertical direction in relation to the hot rolling direction is 980 MPa or more.
[00179] Furthermore, the steel sheet excellent in low temperature toughness indicates a steel sheet whose fracture transition temperature (vTrs) of a Charpy test performed in accordance with JIS Z 2242 is -40 ° C, desirably -50 ° C or less, and also desirably -60 ° C or less. In the present invention, the desired steel sheet is used mainly for automobiles, so that its sheet thickness becomes 3 mm or similar in many cases. Thus, when these evaluations are performed, the surface of the hot-rolled and polished steel plate, and the steel plate is worked on a 2.5 mm specimen and the evaluations are performed.
[Examples] [00180] The technical contents of the present invention will be explained while citing examples of the present invention. Note that the conditions in the examples are conditions employed to confirm the applicability and effects of the present invention, and the present invention is not limited to those examples. The present invention can employ several conditions as long as the aim of the present invention is achieved without departing from the spirit of the present invention.
[00181] Hereinafter, the results of the exams using the steels A to S that satisfy the condition of the composition of the present invention and the steels a to k that do not satisfy the condition of the composition of the present invention illustrated in Table 1 will be explained as examples. Note that specifically La and Ce are used as REM.
[00182] After these steels were cast, they were either heated directly to a temperature range of 1030 ° C to 1300 ° C, or they were cooled once to room temperature and then re-heated to the temperature range, and later hot rolling was performed under each of the conditions in Table 2-1 and Table 2-2, finishing rolling at 760 at 1030 ° C, cooling and winding were performed under each of the conditions illustrated in Table 2-1 and Table 2-2, and hot-rolled steel sheets having a thickness of 3.2 mm each. Subsequently, stripping was carried out, and then skin pass lamination was carried out at a reduction rate of 0.5%.
[00183] Several specimens were cut from the obtained hot-rolled steel sheets, and a material test, an observation of the structure, etc. were performed.
[00184] As a tensile test, a JIS No. 5 specimen was cut in a vertical direction to the rolling direction, and the test was performed in accordance with JIS Z 2242.
[00185] As a measurement of the amount of hardening in cooking, a JIS No. 5 specimen was cut in a vertical direction to the rolling direction, and the measurement was performed in accordance with the test method of a hardening test in cooking of paint described in an appendix to JIS G 3135. The amount of pre-tension has been adjusted to 2%, and the heat treatment condition has been adjusted to 17 °° CX 20 minutes.
[00186] The Charpy test was performed in accordance with JIS Z 2242, and the transition temperature of fracture appearance was measured. The thickness of the steel sheet of the present invention was less than 10 mm, so that the front and rear surfaces of the obtained hot-rolled steel sheets were polished to a thickness of 2.5 mm, and subsequently the Charpy test was performed .
[00187] As for some of the steel sheets, they were heated to 660 to 720 ° C and were subjected to a hot dip galvanizing treatment or a bonding heat treatment at 540 to 580 ° C after the treatment of galvanization, and hot dip galvanized steel sheets (GI) or bonded hot dip galvanized steel sheets (GA) were obtained, and subsequently a material test was performed.
[00188] The microstructure observation was performed by the method described above, and the volume fraction of each structure, the numerical density of the iron-based carbides, the diameter of the effective crystal grain and the aspect ratio were measured.
[00189] The results are shown in Table 3-1 and Table 3-2. [00190] It is found that only those that satisfy the conditions of the present invention have a maximum tensile strength of 980 MPa or more excellent low temperature toughness.
[00191] On the other hand, as for A-3, B-4, E-4, J-4, M-4, and S-4, where the heating temperature of the plate was less than 1200 ° C, carbides of Ti and Nb that precipitated during casting did not melt easily, so that even if the other hot rolling conditions were adjusted to be in the ranges of the present invention, it was not possible to make the structural fraction and the effective crystal grain diameter drop within the ranges of the present invention and low temperature resistance and toughness deteriorated.
[00192] As for steels A-4, E-5, J-5, and M-5, the temperature of the rough rolling mill was 1100 ° C or more, the grain diameter of the austenite became very rough, and the diameter of the crystal grain of the tempered martenite after processing or the lower bainite also became rough, and therefore the low temperature toughness deteriorated.
As for A-5, B-6, J-6, M-6, and S-6 steels, heating was not carried out before the finishing lamination after the roughing lamination was completed, and therefore the recrystallization of the austenite was not able to progress and the aspect ratio of the effective crystal grains of the tempered martensite after the transformation of the lower bainite became greater than 2, and therefore the tenacity at low temperature deteriorated.
[00193] As for steels A-6, B-7, J-7, M-7, and S-7, the temperature of the finishing lamination was very low and the lamination was carried out in a non-recrystallized austenite region, and thus the grains were extended in the lamination direction, resulting in the fact that the aspect ratio was large and the low temperature toughness deteriorated.
As for A-7, B-8, J-8, M-8, and S-8 steels, the average cooling rate from the temperature of the finishing laminate to 400 ° C was less than 50 ° C / s, ferrite was formed in large quantities during cooling to make it difficult to guarantee resistance, and an interface between ferrite and martensite became a starting point for destruction, and therefore low temperature toughness deteriorated.
[00195] As for A-8 steel, the winding temperature was 480 ° C, which was high, and the steel sheet structure became a superior Bainite structure, and therefore it became difficult to guarantee the maximum tensile strength of 980 MPa or more, and crude iron-based carbides that precipitated between the trusses that exist in the upper Bainite structure became the starting points of destruction, resulting in the fact that the low temperature toughness deteriorated.
[00196] As for steels B-9 and J-9, the winding temperature was 580 to 620 ° C, which was high, and the steel plate structure became a mixed structure of ferrite and perlite. As a result, it was difficult to guarantee the maximum tensile strength of 980 MPa or more, and an interface between the ferrite in the pearlite and the iron-based carbide became a starting point of destruction, and therefore the low temperature toughness deteriorated.
[00197] As for M9 steel, the winding temperature was the ambient temperature, which was low, and the steel plate structure became tempered martensite and new martensite, and therefore the new martensite became a starting point of destruction, resulting in the fact that the low temperature toughness has deteriorated.
[00198] Furthermore, as illustrated in steels A-9 and 10, B-10 and 11, E-6 and 7, J-10 and 11, M-10 and 11, and S-9 and 10, it was possible to confirm that the quality of the material of the present invention was able to be guaranteed even when the hot dip galvanizing treatment or the linked hot dip galvanizing treatment was carried out.
[00199] On the other hand, regarding aak steels, where the steel plate components do not satisfy the ranges of the present invention, it was not possible to obtain the maximum tensile strength of 980 MPa or more and excellent low temperature toughness that were determined in the present invention.
[00200] Incidentally, when a sample was manufactured under the same condition as that of A-3 steel except that the cooling rate from 550 to 400 ° C was adjusted to 45 ° C / s, the average rate of cooling from temperature of the finishing laminate up to 400 ° C was 73 ° C / s, and therefore the average cooling rate satisfied 50 ° C / s or more. However, the upper bainite became 10% or more and variations were also caused in the quality of the material. In addition, when attempting to manufacture a sample under the same conditions as A-1 steel except that the O content exceeded 0.01% by mass, there was a problem with the workability, and it was confirmed that it cannot be treated as a product.
[Table 1] - Chemical composition (% by mass) [Table 2-1] - Hot rolling conditions i Underlined value means being outside the range of the present invention R denotes hot rolled steel sheet, GI denotes galvanized steel sheet by hot-dip, GA denotes hot-dip galvanized steel sheet bonded to hot-rolled steel plate.
Each underlined value means to be outside the range of the present invention Industrial applicability [00201] According to the present invention, it becomes possible to be used in a very cold place, and therefore its industrial contribution is extremely notable.

权利要求:
Claims (10)
[1]
1. Hot-rolled steel sheet, characterized by the fact that it comprises: a structure that is a composition containing, in mass%, C: 0.01 to 0.2%; Si: 2.5% or less (not including "0" (zero)); Mn: 4.0% or less (not including "0" (zero)); P: 0.10% or less; S: 0.03% or less; Al: 0.001 to 2.0%; N: 0.01% or less (not including "0" (zero)); O: 0.01% or less (not including "0" (zero)); Ti: 0.03 to 0.30%; Nb: "0" (zero) at 0.30%; Cu: "0" (zero) at 2.0%; Ni: "0" (zero) at 2.0%; Mo: "0" (zero) at 1.0%; V: "0" (zero) at 0.3%; Cr: "0" (zero) at 2.0%; Mg: "0" (zero) at 0.01%; Ca: "0" (zero) at 0.01%; REM: "0" (zero) at 0.1%; B: "0" (zero) at 0.01%; and the balance being composed of iron and impurities; and in which, in a fraction of volume, 90% or more of tempered martensite with conformed grains, or in a fraction of volume, 90% or more in total of both, tempered martensite with conformed grains and lower bainite are contained and the aspect ratio average of tempered martensite and lower bainite is 2 or less.
[2]
2. Hot-rolled steel sheet according to claim 1, characterized by the fact that the diameter of the effective crystal grain of tempered martensite and lower bainite is 10 pm or less.
[3]
3. Hot-rolled steel sheet, according to claim 1 or 2, characterized by the fact that 1 χ 106 (pieces / mm2) or more of iron-based carbides exist in tempered martensite and lower bainite.
[4]
4. Hot-rolled steel sheet according to any of claims 1 to 3, characterized by the fact that it also comprises, in mass%: Nb: 0.01 to 0.30%.
[5]
5. Hot-rolled steel sheet according to any one of claims 1 to 4, characterized by the fact that it further comprises, in mass%: one element or two or more elements selected from the group consisting of: Cu: 0, 01 to 2.0%; Ni: 0.01 to 2.0%; Mo: 0.01 to 1.0%; V: 0.01 to 0.3%; and Cr: 0.01 to 2.0%.
[6]
6. Hot-rolled steel sheet according to any one of claims 1 to 5, characterized by the fact that it further comprises, in mass%: one element or two or more elements selected from the group consisting of: Mg: 0, 0005 at 0.01%; Ca: 0.0005 to 0.01%; and REM: 0.0005 to 0.1%.
[7]
7. Hot-rolled steel sheet according to any of claims 1 to 6, characterized by the fact that it also comprises, in mass%: B: 0.0002 to 0.01%.
[8]
8. Hot-rolled steel sheet according to any one of claims 1 to 7, characterized in that a galvanized layer or a bonded galvanized layer is included in a surface of the hot-rolled steel sheet.
[9]
9. Method of producing a hot-rolled steel sheet, characterized by the fact that it comprises: melting a steel having a composition containing, in mass%: C: 0.01 to 0.2%; Si: 2.5% or less (not including "0" (zero)); Mn: 4.0% or less (not including "0" (zero)); P: 0.10% or less; S: 0.03% or less; Al: 0.001 to 2.0%; N: 0.01% or less (not including "0" (zero)); O: 0.01% or less (not including "0" (zero)); Ti: 0.03 to 0.30%; Nb: "0" (zero) at 0.30%; Cu: "0" (zero) at 2.0%; Ni: "0" (zero) at 2.0%; Mo: "0" (zero) at 1.0%; V: "0" (zero) at 0.3%; Cr: "0" (zero) at 2.0%; Mg: "0" (zero) at 0.01%; Ca: "0" (zero) at 0.01%; REM: "0" (zero) at 0.1%; B: "0" (zero) at 0.01%; and the balance being composed of iron and impurities; cast the steel on a slab, and then directly heat the slab to 1200 ° C or more or cool the slab once and then heat the slab to 1200 ° C or more; perform hot rolling where the rolling reduction ratio in the final roughing lamination step is set to 25% or more and the rolling temperature is set to less than 1100 ° C and the roughing lamination is completed, the part obtained from the roughing lamination is heated to 10 ° C or more before the finishing lamination, and the finishing temperature of the finishing lamination to be carried out subsequently is adjusted to 900 ° C or more; and perform cooling at an average cooling rate of 50 ° C / s or more from the finish temperature of the finishing laminate to 400 ° C and perform winding at 100 ° C or more at less than 400 ° C.
[10]
10. Hot-rolled sheet production method, according to claim 9, characterized by the fact that it also comprises: performing the galvanizing treatment or the galvanostegia treatment after winding.

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MX2015014099A|2015-12-15|

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CN105209650A|2015-12-30|

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US20190161820A1|2019-05-30|

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EP2998414B1|2019-04-24|

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JPWO2014185405A1|2017-02-23|

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WO2014185405A1|2014-11-20|

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CN105209650B|2017-11-07|

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PL2998414T3|2019-08-30|

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KR101709432B1|2017-03-08|

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BR112015024854A2|2017-07-18|

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US20160273066A1|2016-09-22|

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TW201446973A|2014-12-16|

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US10260124B2|2019-04-16|

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TWI509084B|2015-11-21|

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EP2998414A4|2017-01-04|

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法律状态:
2018-11-13| B06F| Objections, documents and/or translations needed after an examination request according [chapter 6.6 patent gazette]|

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2019-06-11| B06A| Patent application procedure suspended [chapter 6.1 patent gazette]|

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2019-09-10| B25D| Requested change of name of applicant approved|Owner name: NIPPON STEEL CORPORATION (JP) |

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2020-01-14| B09A| Decision: intention to grant [chapter 9.1 patent gazette]|

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2020-03-10| B16A| Patent or certificate of addition of invention granted [chapter 16.1 patent gazette]|Free format text: PRAZO DE VALIDADE: 20 (VINTE) ANOS CONTADOS A PARTIR DE 13/05/2014, OBSERVADAS AS CONDICOES LEGAIS. |

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2022-03-08| B21F| Lapse acc. art. 78, item iv - on non-payment of the annual fees in time|Free format text: REFERENTE A 8A ANUIDADE. |

优先权:

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申请号 | 申请日 | 专利标题

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JP2013102144|2013-05-14|

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JP2013-102144|2013-05-14|

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PCT/JP2014/062701|WO2014185405A1|2013-05-14|2014-05-13|Hot-rolled steel sheet and production method therefor|

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