TW201318820A - High strength galvanized hot rolled steel sheet and method for producing the same - Google Patents

Abstract

The high strength galvanized hot- rolled steel sheet of the invention has a plating film on at least one surface of a hot hot-rolling rolled steel sheet that serves as a substrate. The hot hot-rolling rolled steel sheet includes a constitution including C: 0.010% to 0.050%, Si: 0.2% or less, Mn: 0.10% to 0.80%, P: 0.025% or less, S: 0.01% or less, N: 0.01% or less, Al: 0.1% or less, Ti: 0.05% to 0.10% by mass%, satisfying Ti*/48 < C/12 and Ti*=Ti-( N/14x48+S/32x48) (C, S, N, and Ti satisfy a content of each element(mass%)), and the rest including Fe and unavoidable impurities; a matrix that an area ratio of a ferrite phase compared to the whole structure is 95% or more; and a structure that is formed by dispersed precipitation of fine carbides including Ti, wherein the average particle size of the fine carbides is less than 10 nm. The high-strength galvanized hot hot-rolled steel sheet has a tensile strength of 590 MPa or more and excellent workability.

Description

High-tension hot-rolled steel plate and manufacturing method thereof

The present invention relates to a high strength galvanized hot rolled steel sheet and method for producing the same, which is suitable for a conveying device for an automobile part or the like and a material for a building material.

From the viewpoint of protecting the environmental environment, it is often important in the automotive industry to reduce the amount of CO ₂ emissions, to maintain the strength of the vehicle body, to reduce the weight of the vehicle body, and to improve the fuel consumption of the automobile. Question. In order to reduce the weight of the vehicle body while maintaining the strength of the vehicle body, it is effective to reduce the thickness of the steel sheet by increasing the strength of the steel sheet for the material for automobile parts. In particular, the high strength and thinning of the steel plate for the chassis parts of automobiles makes the automobile body significantly lighter, and thus is an extremely effective means for improving the fuel consumption of the automobile. Therefore, the expectation of high strength of the materials for these parts is very strong.

Moreover, automotive parts, especially chassis parts, are mostly exposed to corrosive environments, so steel sheets for automotive parts must also have the desired corrosion resistance. Therefore, as a steel sheet for automobile parts, a high-tensile (hot-rolled) plated steel sheet excellent in corrosion resistance is widely used.

On the other hand, most of the automobile parts using steel sheets as materials are formed by press working or burring processing, and therefore, it is required to have excellent elongation and stretchability for steel sheets for automobile parts (stretch-flange) Processability such as formability). For example, because of the chassis zero In the steel sheet which is a material for the chassis parts, the strength and the corrosion resistance together with the workability are taken into consideration, and the high tension (hot rolling) excellent in workability such as the stretchability and the bending workability is sought. ) Plated steel.

However, in general, the steel material is accompanied by high strength and the workability is lowered. The workability of high tension (hot rolled) plated steel sheets is much worse than that of ordinary soft steel sheets. Therefore, in order to apply a high-tensile (hot-rolled) steel sheet to a chassis component or the like, development of a high-tension (hot-rolled) steel sheet (a steel sheet to be a base material for plating a steel sheet) having both strength and workability is required. Various studies have been conducted so far, and various techniques have been proposed.

For example, Patent Document 1 proposes a technique of containing carbon (C): 0.03% to 0.25%, cerium (Si): 2.0% or less, and manganese (Mn) in terms of % by weight: 2.0% or less, phosphorus (P): 0.1% or less, sulfur (S): 0.007% or less, aluminum (Al): 0.07% or less, and chromium (Cr): 1.0% or less; and it is set to contain ferrite (ferrite) And the composite structure of the second phase, by specifying the hardness, volume ratio, and particle diameter of the second phase, thereby improving the high-strength hot-rolled steel sheet having a tensile strength (TS) of more than 490 N/mm ² (490 MPa). Fatigue property and extension. The second phase is one or more of pearlite, bainite, martensite, and retained austenite.

However, in the technique proposed in Patent Document 1, when the steel sheet is subjected to press working or the like and formed into a desired part shape, the interface between the soft ferrite iron and the hard second phase is likely to be a starting point of cracking during processing. Therefore, there is a problem of unstable workability. Moreover, Patent Document 1 proposes In the technique of the steel sheet, when the tensile strength of the steel sheet is increased to the order of 590 MPa, the problem of deterioration in workability and particularly stretchability is also found.

Further, Patent Document 2 proposes a technique of including C: 0.01% to 0.10%, Si: 1.5% or less, and Mn: more than 1.0% to 2.5%, in terms of wt%, P. : 0.15% or less, S: 0.008% or less, Al: 0.01% to 0.08%, and a total of one or two types of titanium (Ti) and niobium (Nb): 0.10% to 0.60%; That is, the amount of ferrite is 95% or more in area ratio, and the average crystal grain size of ferrite is 2.0 μm to 10.0 μm, and does not contain granulated iron and retained austenite; thereby increasing the tensile strength to 490 MPa. The fatigue strength and especially the edge of the above high-strength hot-rolled steel sheet. Further, in the technique proposed in Patent Document 2, by setting the Mn content to more than 1.0% to 2.5%, the strength of the steel sheet can be improved and fine fine iron particles can be obtained.

However, in the technique proposed in Patent Document 2, since the Mn content of the steel sheet is high, Mn is segregated toward the center portion of the thickness of the steel sheet, and cracks are generated during the press forming of the steel sheet, so that the steel sheet cannot be stably formed. A problem of excellent stretchability is obtained. Further, in the technique proposed in Patent Document 2, Ti is formed to have a predetermined content to form Ti carbide, whereby the solid solution C which adversely affects the edge resistance can be reduced, but it is contained with respect to C. Excess Ti is likely to coarsen the Ti carbide, and it has been found that there is a problem that the desired strength cannot be stably obtained.

Further, Patent Document 3 proposes a technique of including C: 0.01% to 0.1%, S≦ 0.03%, N≦0.005%, Ti: 0.05% to 0.5%, Si in terms of mass%. : 0.01% to 2%, Mn: 0.05% to 2%, P≦0.1%, Al: 0.005% to 1.0%, and further satisfy the range of Ti-48/12C-48/14N-48/32S≧0% Ti is contained; the average size of precipitates containing 5 nm or more of Ti in the steel is set to 10 ¹ nm to 10 ³ nm, and the minimum interval is set to be more than 10 ¹ nm and 10 ⁴ nm or less. The high-strength hot-rolled steel sheet having a tensile strength of 640 MPa or more has a Burkin formability and a fatigue property.

However, in the technique proposed in Patent Document 3, the distribution of the size of the precipitate contained in the steel sheet is large, and it has been found that there is a problem that the desired strength cannot be stably ensured. Further, in the technique proposed in Patent Document 3, the stretchability of the steel sheet is insufficient.

Prior technical literature Patent literature

Patent Document 1: Japanese Patent Laid-Open No. Hei 4-329848

Patent Document 2: Japanese Patent Laid-Open Publication No. 2000-328186

Patent Document 3: Japanese Patent Laid-Open Publication No. 2002-161340

In the case of a mass-produced automobile part, it is necessary to industrially mass-produce a hot-rolled steel sheet for stably supplying the material of the automobile part, but in the above prior art, it is difficult to stably supply a tensile strength of 590 MPa or more and excellent. High-tensile (hot-rolled) plated steel sheet with workability (extension and bending workability). The present invention advantageously solves the problems faced by the prior art described above, and an object thereof is to provide a high-tensile hot-rolled steel sheet and a method for manufacturing the same, which is suitable as a material for automobile parts, and has a tensile strength of 590 MPa. In addition to the above, it has excellent edge-stretching properties and excellent bending workability, and is excellent in workability.

In order to solve the above problems, the present inventors have actively studied various factors that affect the high strength and workability of the hot-rolled steel sheet, particularly the stretchability and the bending workability. As a result, the following findings were obtained.

1) The steel sheet structure is a single-phase structure of the ferrite-grained iron having excellent dislocation density and excellent workability, and further, when fine carbides are dispersed and precipitated to enhance precipitation, the elongation and bending workability of the hot-rolled steel sheet are maintained. At the same time, the strength is improved.

2) In order to obtain a high-strength hot-rolled steel sheet having excellent workability and having a tensile strength of 590 MPa or more, it is necessary to disperse fine carbides having an average particle diameter of less than 10 nm which is effective for precipitation strengthening.

3) As a fine carbide which contributes to precipitation strengthening, it is effective as a carbide containing Ti.

4) In the case of the Ti-containing carbide, it is effective to ensure the workability, particularly the bending workability, while achieving the high-strength of the hot-rolled steel sheet and the random dispersion. It is a ratio of increasing the carbide containing Ti which is randomly dispersed and precipitated. On the other hand, in the high strength of the hot-rolled steel sheet, the carbide in any of the above-described precipitation forms is effective.

5) The carbide containing Ti is set to have an average particle diameter of less than 10 nm, and in order to suppress coarsening of the carbide after dispersion and precipitation, it is necessary to control the Ti ^* content with respect to the C content in the steel. (When Ti ^* = Ti - (N / 14 × 48 + S / 32 × 48), C, S, N, and Ti are the contents (% by mass) of each element.)

6) After hot rolling of steel material having a predetermined composition, it is cooled When the hot-rolled sheet which is a base material of the hot-rolled steel sheet is wound and wound, when the temperature is optimal for the precipitation of the Ti-containing carbide, the heat of the carbide mainly dispersed in a row is obtained. Rolling plate.

7) The hot-rolled sheet in which the precipitation of the Ti-containing carbide is suppressed is formed at a temperature lower than the temperature optimum for the precipitation of the Ti-containing carbide, and the hot-rolled sheet is specified. The annealing temperature is subjected to a continuous annealing treatment, whereby the Ti-containing carbide is randomly precipitated during the continuous annealing treatment, thereby obtaining a hot-rolled steel sheet containing a large amount of randomly dispersed precipitated carbide (a substrate for hot-rolled steel sheet) And is the substrate before plating after annealing).

The present invention has been completed based on the above findings, and the gist thereof is as follows.

[1] A high-tensile hot-rolled steel sheet comprising: a coating film on at least one surface of a hot-rolled steel sheet as a substrate, wherein the hot-rolled steel sheet has a mass %, so that C, S, N, and Ti satisfy The method of the formula (1) includes C: 0.010% or more and 0.050% or less, Si: 0.2% or less, Mn: 0.10% or more, 0.80% or less, P: 0.025% or less, S: 0.01% or less, and N: 0.01. % or less, Al: 0.1% or less, Ti: 0.05% or more, 0.10% or less, and the remainder contains a composition of Fe and unavoidable impurities; the matrix of the ferrite-grained iron phase with respect to the entire area of the structure is 95% or more. And a structure obtained by dispersing and depositing fine carbides containing Ti and having an average particle diameter of less than 10 nm; and tensile strength of 590 MPa or more, Ti ^* /48<C/12 (1) here, Ti ^* = Ti - (N / 14 × 48 + S / 32 × 48) (C, S, N, Ti: content (% by mass) of each element).

[2] The high-tensile hot-rolled steel sheet according to the above [1], in addition to the above-described composition, contains boron (B): 0.0035% or less, in terms of mass%, and further satisfies the following formula (2). 0.0003-0.00025Mn (2) (Mn, B: content (% by mass) of each element).

[3] The high-tensile hot-rolled steel sheet according to [2], wherein the B is 0.0003% or more and 0.0020% or less.

[4] The high-tensile hot-rolled steel sheet according to the above [1] or [2], wherein the ratio of the number of precipitates of the fine carbides in the columnar form to the number of random precipitates is the following (3) formula: Pr/Ps ≧ 0.8 (2) (Pr: the number of fine carbides which are randomly deposited) (Ps: the number of fine carbides precipitated in a row).

[5] The high-tensile hot-rolled steel sheet according to the above [1] or [2], wherein the volume ratio of the fine carbide to the entire structure is 0.0005 or more.

[6] The high-tensile hot-rolled steel sheet according to [5], wherein the volume ratio is 0.0005 or more and 0.003 or less.

[7] The high-tensile hot-rolled steel sheet according to the above [1] or [2], in addition to the above composition, further contains, by mass%, Cu, Sn, Ni, Ca, Mg, Co, in a total amount of 1% or less. Any one or more of As, Cr, W, Nb, Mo, V, Pb, and Ta.

[8] A method for producing a high-tensile hot-rolled steel sheet, wherein the steel material is subjected to hot rolling including rough rolling and finish rolling, and after completion of the finish rolling, cooling and winding are performed to form a hot-rolled sheet, and the hot rolling is performed. The plate is sequentially subjected to continuous annealing treatment and plating treatment to form a hot-rolled steel sheet, and the steel material includes: in mass%, C, S, N, and Ti satisfy the following formula (1), and the quality is %: C: 0.010% or more, 0.050% or less, Si: 0.2% or less, Mn: 0.10% or more, 0.80% or less, P: 0.025% or less, S: 0.01% or less, N: 0.01% or less, Al: 0.1 % or less, Ti: 0.05% or more and 0.10% or less, and the remainder contains a composition of Fe and unavoidable impurities; the finish rolling temperature of the finish rolling is set to 880 ° C or higher, and the average cooling rate of the above cooling is set to 10 ° C / s or more, the winding temperature is 400 ° C or more and less than 550 ° C, and the annealing temperature of the continuous annealing treatment is 550 ° C or more and 750 ° C or less, and the tensile strength is 590 MPa or more, Ti ^* /48 < C / 12... (1) Here, Ti ^* = Ti - (N / 14 × 48 + S / 32 × 48) (C, S, N, Ti: content (% by mass) of each element).

[9] In the method for producing a high-tensile hot-rolled steel sheet according to the above [8], in addition to the above-described composition, in a mass%, and further satisfying the following formula (2), B: 0.0035% or less, B≧ 0.0003-0.00025Mn (2) (Mn, B: content (% by mass) of each element).

[10] The method for producing a high-tensile hot-rolled steel sheet according to [9], wherein the B is 0.0003% or more and 0.0020% or less.

[11] The method for producing a high-tensile hot-rolled steel sheet according to the above [8] or [9], in addition to the above composition, further contains, by mass%, Cu, Sn, Ni, Ca, and Mg in a total amount of 1% or less. , Co, As, Cr, W, Nb, Mo, V, Any one of Pb and Ta.

According to the present invention, it is possible to industrially stably produce a high-tensile hot-rolled steel sheet which is suitable as an material for automobile parts, and has a tensile strength of 590 MPa or more, and has a function as an industrially obvious effect. Materials such as chassis parts having a complicated cross-sectional shape at the time of pressing are excellent in workability (stretching property and bending workability).

Hereinafter, the present invention will be described in detail.

First, the reason for limiting the structure and carbide of the hot-rolled steel sheet which is the substrate of the high-tensile hot-rolled steel sheet according to the present invention will be described.

The hot-rolled steel sheet as the substrate of the high-tensile hot-rolled steel sheet according to the present invention has a matrix in which the ferrite-grained iron phase is 95% or more with respect to the area ratio of the entire structure, and a Ti-containing material having an average particle diameter of less than 10 nm. The fine carbide is dispersed and precipitated in the matrix. The fine carbide is preferably a carbide having a ratio of the number Ps of the columnar precipitates to the number Pr of the random precipitates satisfying Pr/Ps ≧ 0.8. Further, it is preferable that the volume ratio of the fine carbide to the entire structure is 0.0005 or more.

Fertilizer iron phase: 95% or more based on the area ratio of the whole tissue

In the present invention, it is necessary to form a ferrite-particle iron phase in terms of ensuring workability (stretching property and bending workability) of the hot-rolled steel sheet. In the improvement of the workability of the hot-rolled steel sheet, it is effective to set the structure of the hot-rolled steel sheet which is a substrate of the hot-rolled steel sheet to a ferrite-grain iron phase which is low in dislocation density and excellent in elongation. In particular, for the improvement of the edge-stretching property, it is preferred to heat-roll the above The structure of the steel sheet is a single-phase structure of the ferrite-iron, but even in the case of a single-phase structure of the ferrite-free iron, as long as it is substantially a single-phase structure of the ferrite-iron, that is, as long as it is relative to the whole of the structure When the area ratio is 95% or more, it is the ferrite-grain iron phase, and the above effects can be fully exerted. Therefore, the area ratio of the ferrogranular iron phase to the entire structure is set to 95% or more.

Further, in the hot-rolled steel sheet, as the phase other than the ferrite-grained iron phase, a cementite, a buckling iron, a toughened iron phase, a granulated iron phase, and a retained austenite may be used, as long as they are the same. The total amount is about 5% or less with respect to the area ratio of the entire structure, and can be tolerated.

Fine carbide containing Ti

Ti is a strong carbide constituent element, and the carbide containing Ti tends to be a fine carbide having an extremely small average particle diameter. In the present invention, the high-strength of the hot-rolled steel sheet is obtained by dispersing and depositing the fine carbide in the hot-rolled steel sheet as the substrate of the hot-rolled steel sheet, and the fineness is dispersed and precipitated in the hot-rolled steel sheet. The carbide is a fine carbide containing Ti.

Average particle size of fine carbide: less than 10 nm

In order to impart a desired strength (tensile strength: 590 MPa or more) to the hot-rolled steel sheet, the average particle diameter of the fine carbides which are deposited and deposited in the hot-rolled steel sheet which is the substrate of the hot-rolled steel sheet is extremely important. In the invention, the average particle diameter of the fine carbide containing Ti is set to be less than 10 nm. When fine carbides are precipitated in the matrix, the fine carbides act as resistance against the movement of dislocations generated when the deformation is applied to the steel sheet, whereby the hot-rolled steel sheet is strengthened, and the average grain of the fine carbides is increased. The path is set to less than 10 Nm, the above effect is more significant. Therefore, the average particle diameter of the fine carbide containing Ti is set to be less than 10 nm. More preferably 5 nm or less.

The ratio of the number Ps of fine carbides precipitated in a columnar form to the number Pr of randomly deposited fine carbides: Pr/Ps ≧ 0.8

In the carbides (fine carbides) containing Ti, the precipitates are dispersed in a fixed direction and randomly dispersed, and the fine carbides dispersed and precipitated in the column form the bending workability of the hot-rolled steel sheet. Bad effects. This is because the interface between the fine carbide and the substrate becomes a crack generating portion at the time of bending, and if the fine carbides are dispersed and precipitated in a row, the crack generated at the interface between the fine carbide and the substrate easily spreads.

For the reason of the above, in the present invention, it is preferable to increase the ratio of the finely precipitated fine carbides in the hot-rolled steel sheet finally obtained, thereby suppressing deterioration of the bending workability of the hot-rolled steel sheet. The ratio Pr/Ps of the number Ps of the fine carbides precipitated in the columnar form and the number Pr of the finely precipitated fine carbides is preferably 0.8 or more.

In order to stably obtain the strength of the hot-rolled steel sheet, it is effective to control the amount of dispersion of fine carbides which are dispersed and precipitated in the hot-rolled steel sheet which is a substrate of the hot-rolled steel sheet. In the present invention, it is preferable to contain Ti. Further, the fine carbide having an average particle diameter of less than 10 nm is dispersed in a volume ratio of 0.0005 or more to the entire hot-rolled steel sheet structure. However, when the volume ratio exceeds 0.003, the strength is too high and the edge-strengthening property is lowered. Therefore, the volume is preferably 0.0005 or more and 0.003 or less.

Next, the heat of the substrate as the high-tensile hot-rolled steel sheet of the present invention The reason for limiting the composition of the rolled steel sheet will be described. In addition, the % which shows the following component composition means the mass % unless it demonstrates especially.

C: 0.010% or more and 0.050% or less

C is an essential element for strengthening steel in forming fine carbides. When the C content is less than 0.010%, fine carbides cannot be sufficiently ensured, and tensile strength of 590 MPa or more cannot be obtained. On the other hand, when the C content exceeds 0.050%, the ferrite is easily formed in the steel sheet, and the stretchability is deteriorated. Therefore, the C content is set to be 0.010% or more and 0.050% or less. It is preferably 0.020% or more and 0.035% or less.

Si: 0.2% or less

Si is a solid solution strengthening element and is an element effective for increasing the strength of steel. However, when the Si content is more than 0.2%, the precipitation of C from the ferrite-rich iron phase is promoted, and coarse Fe carbide is easily precipitated at the grain boundary, and the elongation property is lowered. Moreover, excessive Si adversely affects plating properties. Therefore, the Si content is set to 0.2% or less. It is preferably 0.05% or less. Further, in order to solid solution strengthening, it is preferably 0.005% or more.

Mn: 0.10% or more and 0.80% or less

Mn is a solid solution strengthening element and is an element effective for increasing the strength of steel. In order to obtain the above effects, it is preferable to contain 0.10% or more, and if the Mn content exceeds 0.80%, segregation is likely to occur, and a phase other than the ferrite-grained iron phase, that is, a hard phase is formed, and the edge-hanging property is lowered. Therefore, the Mn content is set to be 0.10% or more and 0.80% or less. It is preferably 0.10% or more and 0.5% or less. More preferably, it is 0.10% or more and 0.45% or less.

P: 0.025% or less

P is a solid solution strengthening element and is an element effective for increasing the strength of steel. When the P content exceeds 0.025%, segregation is remarkable, and the elongation is lowered. Therefore, the P content is set to 0.025% or less. It is preferably 0.02% or less. Further, in order to solid solution strengthening, it is preferably 0.005% or more.

S: 0.01% or less

S is an element which lowers hot workability (hot rolling property), and in addition to improving the hot-tearing sensitivity of a slab, it is present as manganese sulfide (MnS) in steel, thereby making the hot rolled steel sheet The elongation of the edge deteriorates. Therefore, in the present invention, it is preferable to reduce S as much as possible and to set it to 0.01% or less. It is preferably 0.005% or less.

N: 0.01% or less

N is a harmful element in the present invention, and it is preferred to reduce it as much as possible. In particular, if the N content exceeds 0.01%, the coarse nitride is formed in the steel, so that the stretchability is lowered. Therefore, the N content is set to 0.01% or less. It is preferably 0.006% or less.

Al: 0.1% or less

Al is an element that functions as an oxygen scavenger. In order to obtain this effect, it is preferable to contain 0.001% or more, and the content of more than 0.1% lowers workability (stretching property and bending workability). Therefore, the Al content is set to 0.1% or less.

Ti: 0.05% or more and 0.10% or less

Ti is one of the most important elements in the invention. Ti is an element which contributes to the high strength of the steel sheet while maintaining excellent edge-strength and bending workability by forming carbide. In order to achieve the above effects, it is desirable to contain 0.05%. the above. However, when the Ti content exceeds 0.10%, the edge-strengthening property tends to decrease, and thus the Ti content is made 0.10% or less. It is preferably 0.05% or more and 0.095% or less.

The hot-rolled steel sheet which is a substrate of the high-tensile hot-rolled steel sheet of the present invention contains C, S, N, and Ti so as to satisfy the formula (1) within the above range.

Ti ^* /48<C/12.........(1)

Here, Ti ^* = Ti-(N/14×48+S/32×48)

(C, S, N, Ti: content of each element (% by mass))

The above formula (1) is a requirement for satisfying the above-described desired precipitation state of the fine carbide containing Ti, and is an extremely important index in the present invention.

As described above, in the present invention, fine carbide containing Ti is dispersed and precipitated in a hot-rolled steel sheet as a substrate. Here, the carbide containing Ti tends to be a fine carbide having an extremely small average particle diameter. However, when the Ti bonded to C is C or more in atomic ratio, the carbide is likely to be coarsened. Further, with the coarsening of the carbide, it is difficult to secure the desired strength of the steel sheet (tensile strength: 590 MPa or more). Therefore, in the present invention, it is necessary to make the atomic % (C/12) of C contained in the steel material larger than the atomic % (Ti ^* / 48) of Ti which contributes to carbide formation.

Further, in the present invention, a predetermined amount of Ti is added to the steel material, and the fine carbide containing Ti is dispersed and deposited in a hot-rolled steel sheet as a substrate which is melted in the steel material during heating before hot rolling. The carbides are mainly precipitated in the subsequent steps (winding step and continuous annealing step) after the hot rolling. However, not all of the Ti added to the steel material contributes to carbide formation, and a part of Ti added to the steel material is consumed by the formation of nitride or sulfide. This is because, in a temperature range higher than the winding temperature, Ti is more likely to form nitrides or sulfides than in the formation of carbides, and in the production of hot-rolled steel sheets, Ti forms nitrides or sulfides before the winding step. Things. Thus, Ti(Ti ^* ) contributing to carbide formation in Ti added to the steel material can be represented by "Ti ^* =Ti-(N/14×48+S/32×48)”.

For the above reasons, in the present invention, in order to make the atomic % (C/12) of C larger than the atomic % (Ti ^* /48) of Ti which contributes to carbide formation, it is set as Ti ^* =Ti-( N/14×48+S/32×48) contains each element of C, S, N, and Ti so as to satisfy Ti ^* /48<C/12.

When Ti ^* /48 is C/12 or more, the fine carbide containing Ti tends to be coarsened.

Further, the carbide containing Ti is obtained by heating the steel material to the austenite region before hot rolling to melt the carbide in the steel material and to be dispersed and precipitated in the subsequent hot rolling step. At this time, the transformation temperature from austenite to fermented iron is adjusted to a temperature suitable for precipitation of carbide containing Ti, and when wound at this temperature, simultaneous with austenite→fertilizer iron metamorphism, The fine carbides containing Ti are precipitated in a row (phase interface precipitation).

Here, if the steel material is transformed from austenite to ferrite iron at a high temperature, carbides containing Ti are precipitated in a high temperature region, so that carbides precipitated in a high temperature region are easily coarsened, and thus the desired fineness cannot be obtained. Carbide (average particle size less than 10 nm). Therefore, in the present invention, it is preferred to make the steel material The temperature at which austenite deforms to the ferrite is reduced to a temperature sufficient to precipitate fine carbides.

Therefore, in the present invention, in order to lower the temperature of the austenite→fertilizer iron metamorphism, in addition to the above-described composition, B (0.0035% or less) may be contained in a form satisfying the following formula (2).

B≧0.0003-0.00025Mn.........(2)

(Mn, B: content of each element (% by mass))

B: 0.0035% or less

B is an element which lowers the austenite→fertilizer iron metamorphic temperature of the steel. In the present invention, by adding B, the austenite→fertilizer iron metamorphic temperature of the steel is lowered, so that the fineness of the carbide containing Ti can be realized. Chemical. In order to obtain the above effects, it is preferred to set the B content to 0.0003% or more. On the other hand, even if it exceeds 0.0035%, the above effect is saturated. Therefore, the B content is preferably set to 0.0035% or less. More preferably, it is 0.0003% or more and 0.0020% or less.

B≧0.0003-0.00025Mn.........(2)

(Mn, B: content of each element (% by mass))

In the present invention, in the case where B is contained, it is also important to control the ratio of the B content to the Mn content in the steel within an appropriate range. The present inventors have studied the following method, that is, in the ferrite grain iron phase relative to the tissue as a whole In the matrix having an area ratio of 95% or more, the Ti-containing carbide is finely dispersed (average particle diameter of less than 10 nm). As a result, the following new findings were obtained: in the temperature range suitable for the precipitation of fine carbides containing Ti, the austenite→fertilizer iron metamorphic temperature of the cooling process after the end of hot rolling was adjusted (the fat and iron metamorphosis in the CCT diagram) The region is an extremely effective method for refining the carbide containing Ti to an average particle diameter of less than 10 nm.

Further, the inventors of the present invention further studied and found that in the steel composition of the present invention, the steel material is adjusted in such a manner that the B content and the Mn content of the steel material satisfy a desired relationship, whereby the steel can be adjusted within the target range. Austenite → fat iron iron metamorphic temperature. Here, in the above formula, when the value of the right side (0.0003-0.00025Mn) is zero or less, the value on the right side is regarded as zero.

In addition, in the present invention, when the content of Mn as a solid solution strengthening element exceeds 0.35%, the desired steel sheet strength (tensile strength: 590 MPa or more) can be secured without using the effect of the above B. However, when the content of Mn is 0.35% or less, it is difficult to ensure the desired strength of the steel sheet without using the effect of the above B. Therefore, when the content of Mn is 0.35% or less, it is preferable to contain B in order to make the carbide containing Ti finer.

In the hot-rolled steel sheet which is a substrate of the high-tensile hot-rolled steel sheet according to the present invention, Cu, Sn, Ni, Ca, Mg, Co, As, Cr, W, Nb, Mo, V may be contained in a total amount of 1% or less. Any one or more of Pb and Ta. It is preferably 0.1% or less, more preferably 0.03% or less. Further, the components other than the above are Fe and unavoidable impurities.

The high-tensile hot-rolled steel sheet according to the present invention has a plating film on the surface of the hot-rolled steel sheet. By providing a coating, the corrosion resistance of the hot-rolled steel sheet is improved, and a high-tensile hot-rolled steel sheet having high strength and excellent workability and suitable for exposure to parts of a severe corrosive environment, such as chassis parts of automobiles, can be obtained. . The type of the plating film is not particularly limited, and for example, a hot-dip galvanized film or an alloyed hot-dip galvanized film or the like is suitably used.

Next, a method of producing the high-tensile hot-rolled steel sheet according to the present invention will be described.

In the present invention, the steel material having the above composition is subjected to hot rolling including rough rolling and finish rolling, and after completion of the finish rolling, cooling and winding are performed to form a hot rolled sheet, and then the hot rolled sheet is sequentially subjected to continuous annealing treatment. And plating treatment to form a hot rolled steel plate. In the present invention, the finish rolling temperature of the finish rolling is 880 ° C or higher, the average cooling rate of the cooling is 10 ° C / s or more, and the winding temperature of the winding is 400 ° C or higher. The annealing temperature of the continuous annealing treatment is less than 550 ° C, and is 550 ° C or more and 750 ° C or less.

In the present invention, the method of melting the steel material is not particularly limited, and a known melting method such as a converter or an electric furnace can be employed. Further, after melting, it is preferred to form a slab (steel material) by a continuous casting method due to problems such as segregation, but a known casting method such as agglomerate-block rolling method or thin slab continuous casting method may be used. To form a billet. Further, when the slab is hot-rolled after casting, the slab may be reheated by a heating furnace and then rolled to maintain the temperature at a predetermined temperature or higher, or the slab may be heated without being heated. .

The steel material obtained as described above is subjected to heating, rough rolling, and finish rolling. In the present invention, it is necessary to melt the carbide in the steel material before rough rolling. In the invention containing Ti as a carbide forming element, it is preferred to set the heating temperature of the steel material to 1150 ° C or higher. However, if the heating temperature of the steel material becomes too high, the surface is oxidized to generate TiO ₂ to consume Ti, and in the case of forming a steel sheet, a decrease in hardness near the surface is likely to occur, so that the above heating temperature is preferably set. It is below 1300 °C. Further, as described above, the steel material before the rough rolling is maintained at a temperature equal to or higher than the predetermined temperature, and when the carbide in the steel material is melted, the step of heating the steel material before the rough rolling can be omitted. In addition, the rough rolling conditions are not particularly limited.

Finishing temperature: above 880 °C

The appropriateness of the finish rolling temperature is important for maintaining the stretchability and bending workability of the hot rolled steel sheet and for reducing the rolling load of the finish rolling. When the finish rolling temperature is less than 880 ° C, the crystal grains of the surface layer of the hot rolled sheet become coarse, and workability (stretching property, bending workability) is broken. Therefore, the finish rolling temperature is set to 880 ° C or higher. It is preferably 900 ° C or more. Further, when the finish rolling temperature is too high, enthalpy due to the secondary scale on the surface of the hot rolled sheet is likely to occur, and therefore the finish rolling temperature is desirably set to 1000 ° C or lower.

Average cooling rate and winding temperature

The appropriate cooling of the average cooling rate and the winding temperature is extremely important in the present invention. As described above, in the present invention, by defining the composition of the steel material, the austenite → ferrite iron metamorphic temperature of the steel material can be adjusted within a temperature range suitable for precipitation of the carbide containing Ti (CCT) Figure of ferrite iron Metamorphosis area). Here, among the carbides containing Ti, a temperature range which is particularly likely to be precipitated exists in a temperature range suitable for precipitation, and the temperature range is about 600 ° C to 650 ° C. In the temperature range of 600 ° C to 650 ° C, the driving force of carbide formation (the change in the free energy generated by the solid solution Ti and the solid solution C in the steel and the carbide) is large, and the diffusion rate of the atom is increased, thereby containing The carbide of Ti is most likely to precipitate. Therefore, after the completion of the hot rolling, the forced cooling is performed, and the forced cooling is performed in the temperature region (about 600 ° C to 650 ° C) which is most suitable for the precipitation of the carbide containing Ti, and the winding is performed, and austenite is generated at the time of winding. → When the ferrite and iron are metamorphosed, the austenite→fertilizer iron in the winding state is deformed, and substantially the entire amount of Ti in the steel is precipitated as fine carbide.

However, in the carbide of Ti, the carbide which precipitates at the same time as the austenite → ferrite-grain metamorphism (phase interface precipitation) is dispersed and precipitated in a row, which contributes to the improvement of the strength of the steel sheet, but sometimes the processing of the steel sheet Sexual (bending properties) cause adverse effects. Therefore, in the present invention, the average cooling rate after the end of hot rolling is increased, and the winding temperature is defined as the temperature, that is, in the range from the austenite to the metamorphic temperature of the ferrite iron (the fat in the CCT chart) In the range of the grain iron metamorphic zone, and at a temperature lower than the temperature range (about 600 ° C to 650 ° C) which is most suitable for precipitation of fine carbide containing Ti, thereby suppressing the simultaneous transformation with austenite → ferrite The phase interface which is dispersed in the form of a column is precipitated. In addition, in the continuous annealing treatment before the plating treatment in the next step, the fine carbide containing Ti is randomly dispersed and precipitated, thereby achieving high strength of the hot-rolled steel sheet and ensuring workability (especially bending workability).

Average cooling rate: 10 ° C / s or more

After finishing rolling, if the average cold from the finishing temperature to the winding temperature However, when the speed is less than 10 ° C / s, the austenite → ferrite iron metamorphic temperature becomes high, and the Ti-containing carbides are arranged in a row on the hot-rolled sheet and coarsely precipitated. Therefore, the above average cooling rate is set to 10 ° C / s or more. It is preferably 30 ° C / s or more. Moreover, in order to obtain the ferrite iron structure, it is preferably less than 200 ° C / s.

Winding temperature: 400 ° C or more and less than 550 ° C

The appropriateness of the winding temperature is extremely important in that the structure of the hot-rolled steel sheet which is the substrate of the high-tensile hot-rolled steel sheet of the present invention is a desired structure for the entire region in the width direction of the hot-rolled steel sheet. That is, the ferrite-grained iron phase is a matrix having a ratio of 95% or more with respect to the entire area of the structure, and a structure in which fine carbides containing Ti and having an average particle diameter of less than 10 nm are dispersed and precipitated, and random precipitation is improved. The ratio Pr/Ps of the number Pr of fine carbides to the number Ps of fine carbides precipitated in a row.

As described above, when the steel material having the composition of the present invention is hot-rolled and then cooled and wound to form a hot-rolled sheet, it is most suitable for a temperature range in which precipitation of carbide containing Ti (about 600 ° C. When the winding is performed at 650 ° C), the austenite → ferrite iron in the winding state is deformed, and substantially the entire amount of Ti in the steel is precipitated as fine carbides, and the fine carbides are mainly dispersed in a certain fixed direction. Precipitated hot rolled sheet. When the Ti-containing carbide is positively precipitated during the cooling and winding process after the hot rolling, the precipitated form of the carbide contained in the finally obtained hot-rolled steel sheet is mainly precipitated in a row, and the bending is feared. Deterioration of workability.

Therefore, in the present invention, the carbide material is melted by heating the steel material to the austenite region before hot rolling, and the precipitation of the Ti-containing carbide is suppressed in the subsequent winding step to form a hot rolled sheet. And by the heat The rolled sheet is subjected to a predetermined continuous annealing treatment to precipitate fine carbides (Ti-containing carbides) having a desired average particle diameter, and to count the number of randomly deposited fine carbides in the fine carbides (Pr Increase, thereby increasing the above ratio Pr/Ps. As described above, when the carbide containing Ti is precipitated simultaneously with the austenite→fertilizer iron, the precipitated form is in a columnar shape, and if precipitated during the annealing treatment after the metamorphosis is completed, the precipitated form becomes random. Therefore, in the present invention, the columnar precipitation is suppressed by setting the winding temperature low, and random precipitation during the subsequent continuous annealing treatment is promoted.

If the winding temperature is less than 400 ° C, the matrix does not substantially become a single-phase structure of the ferrite-iron, and the desired workability cannot be obtained. On the other hand, when the winding temperature is 550 ° C or higher, fine carbides (carbides containing Ti) are precipitated in a large amount during winding. In addition, the main precipitation form of the fine carbides deposited during the winding is precipitated in a columnar manner in a single direction, and it is difficult to ensure the bending workability of the high-tensile hot-rolled steel sheet. Therefore, the winding temperature is set to 400 ° C or more and less than 550 ° C. It is preferably 450 ° C or more and less than 550 ° C.

By the above steps, Ti added to the steel material at the time of winding is partially precipitated as a carbide, and a hot rolling in which the matrix is substantially a single phase of the ferrite and iron and a part of Ti remains as a solid solution in the matrix is obtained. board. The hot-rolled sheet thus obtained is subjected to a continuous annealing treatment at a predetermined annealing temperature to precipitate fine carbides (Ti-containing carbides) in a desired precipitation form. Further, when the hot-rolled sheet is subjected to continuous annealing treatment, it is preferred to carry out a pickling treatment in advance to remove the surface iron slag. Further, the temperature rising condition when the hot rolled sheet is heated to the annealing temperature is not particularly limited.

Annealing temperature for continuous annealing: 550 ° C or more and 750 ° C or less

When the annealing temperature exceeds 750 ° C, the carbide containing Ti is coarsened and the strength is lowered. Therefore, the annealing temperature is set to 750 ° C or lower. It is preferably 700 ° C or less. On the other hand, when the annealing temperature is less than 550 ° C, the precipitation amount of the fine carbide containing Ti is insufficient, and the desired steel sheet strength cannot be obtained, so the annealing temperature is 550 ° C or higher. It is preferably 600 ° C or more.

In addition, from the viewpoint of promoting precipitation of Ti-containing fine carbides and preventing coarsening thereof, it is preferable to set the holding time (annealing time) at the annealing temperature to 60 s or more and 600 s or less. More preferably, it is 60 s or more and 300 s or less.

The hot rolled sheet after the continuous annealing treatment is supplied to the plating treatment. The type of the plating treatment is not particularly limited, and a previously known plating treatment can be used. The hot-dip galvanizing treatment is particularly preferable, for example, annealing is performed on the continuous annealing plating line at the above-mentioned annealing temperature, and immersed in a galvanizing bath (0.1% Al-Zn or the like) at 480 ° C to form an adhesion amount of 45 g/m ^{2 .} A hot-dip galvanized film (amount of adhesion per one side).

Further, the alloying treatment may be carried out after the plating treatment, and for example, the alloying treatment may be carried out at 520 ° C after the hot-dip galvanizing treatment.

As described above, according to the method of the present invention, by performing the above-described continuous annealing treatment, it is possible to obtain a hot-rolled sheet having a matrix having an area ratio of the ferrite-grained iron phase to the entire structure of 95% or more, and A structure in which fine carbide containing Ti and having an average particle diameter of less than 10 nm is dispersed and precipitated, and a ratio of finely precipitated fine carbides in the fine carbide is high. Moreover, the hot rolled sheet has a tensile strength of 590 MPa or more and exhibits It has excellent workability in excellent edge and bending workability.

Further, the hot-rolled sheet after the continuous annealing treatment is subjected to a plating treatment, or further an alloying treatment, and a plating film (for example, a hot-dip galvanized film or an alloyed hot-dip galvanized film) is formed on the surface thereof, thereby obtaining high. A high-tensile hot-rolled steel sheet having excellent strength and excellent workability and excellent corrosion resistance.

Instance

A steel slab (steel material) having a wall thickness of 250 mm was formed by melting and continuously casting the molten steel of the composition shown in Table 1 by a generally known method. After heating the slabs to 1,250 ° C, the rough rolling is performed, and finish rolling is performed at the finishing rolling temperature shown in Table 2, and after the completion of the finish rolling, in the temperature range from the finishing rolling temperature to the winding temperature The average cooling temperature shown in Table 2 was cooled, and wound at the winding temperature shown in Table 2 to form a hot rolled sheet. After the obtained hot-rolled sheet was pickled to remove surface iron slag, continuous annealing treatment was performed at the annealing temperature shown in Table 2. Next, the hot-rolled sheet after the continuous annealing treatment was immersed in a hot-dip galvanizing bath (composition of a plating bath: 0.1% Al-Zn, bath temperature: 480 ° C) to form an adhesion amount of 45 g/m ² on both sides (per A molten galvanized film of a single-sided adhesion amount is formed to form a hot-dip galvanized steel sheet (hot-rolled steel sheet). Further, a part of the hot-dip galvanized steel sheets (hot rolled numbers b1, d1, h, i, j, k, and l in Table 2) were alloyed at 520 ° C to form alloyed hot-dip galvanized steel sheets.

A test piece was taken from the hot-rolled steel sheet (hot-dip galvanized steel sheet and alloyed hot-dip galvanized steel sheet) obtained as described above, and the structure observation, the precipitate observation, the tensile test, the hole expansion test, and the bending test were performed to determine the fertilizer grain. Surface of iron phase The product ratio, the average particle diameter and volume ratio of the fine carbide containing Ti, and the precipitation form, tensile strength, hole expansion ratio (extension), and ultimate bending radius (bending workability) of the fine carbide. The test method is as follows.

(i) Organizational observation

A test piece was taken from the obtained hot-rolled steel sheet, and the cross-section of the test piece was mechanically ground, and after etching in a nital etching solution (Nital), a scanning electron microscope (SEM) was used to obtain a magnification. : 3,000 times the photograph of the tissue (SEM photograph) obtained at the position of the center of the thickness of the sheet, and the type of the tissue other than the iron phase of the ferrite grain and the iron phase of the fertiliser, and the area ratio of the ferrite-grained iron phase were determined by an image analysis device.

In addition, a film produced from a hot-rolled steel sheet (position at the center of the sheet thickness) was observed at a magnification of 260,000 times by a transmission electron microscope (TEM), and the particle diameter of the fine carbide containing Ti was determined. Volume ratio, and dispersion precipitation morphology.

With respect to the particle diameter of the fine carbide containing Ti, the area of each particle was obtained by image processing based on the observation result of 30 fields of view at 260,000 times, and the particle diameter was determined by an approximate circle. The particle diameter of each of the obtained particles was arithmetically averaged to obtain an average particle diameter.

The α-iron was electrolyzed using 10% acetamidine-1% tetramethylammonium chloride-methanol solution (AA solution), and the weight of the Ti carbide was determined by analyzing the residue of the residue captured by filtration. The volume is determined by the density of Ti carbide (TiC), and the volume is divided by the volume of the melted α-iron, thereby obtaining the volume ratio of the fine carbide containing Ti.

For the dispersion form, 20 shots were taken for each test piece. In the TEM photograph of 260,000 times, the number Ps of the fine carbides observed as a column and the number Pr of the observed irregularities were counted, and Pr/Ps was obtained. In the observation, even if the test piece was inclined to 30°, the fine carbides were not observed as a columnar shape and were randomly precipitated fine carbides.

(ii) Tensile test

From the obtained hot-rolled steel sheet, JIS No. 5 tensile test piece (JIS Z 2201) having a direction perpendicular to the rolling direction as a direction of stretching was used, and a tensile test according to JIS Z 2241 was carried out. Thus, the tensile strength (TS) was measured.

(iii) Hole expansion test

A test piece (size: 130 mm × 130 mm) was taken from the obtained hot-rolled steel plate, and a hole having an initial diameter d ₀ : 10 mm Φ was formed on the test piece by a punching machine by press working. A hole expansion test was carried out using these test pieces. That is, a cone puncher having a vertex angle of 60° is inserted into the hole, and the hole is expanded to measure the diameter d of the hole when the crack penetrates the thickness of the hot-rolled steel sheet (test piece), and The hole expansion ratio λ (%) was calculated by the following formula.

The hole expansion ratio λ(%)={(dd ₀ )/d ₀ }×100

(iv) ultimate bending test

From the obtained hot-rolled steel sheet, a test piece having a width of 50 mm and a length of 100 mm in the longitudinal direction with respect to the direction perpendicular to the rolling direction was used, and the apex angle was 90° in accordance with JIS Z 2248 (2006). V-bending test (V-Block Method), the most crack-free The ratio R/t of the small bending radius R (mm) to the sheet thickness t (mm) is measured as the ultimate bending radius.

The results obtained are shown in Table 3.

In the examples of the present invention, tensile strength TS: 590 MPa or higher is formed. The hot-rolled steel sheet having the strength and the hole expansion ratio λ: 100% or more and the bending workability of the bending radius of 0.9 or less. On the other hand, the comparative example which is beyond the scope of the present invention cannot ensure a predetermined high strength, or cannot ensure the hole expansion ratio λ or the limit bending radius.

Claims (11)

A high-tensile hot-rolled steel sheet comprising: a coating film on at least one surface of a hot-rolled steel sheet as a substrate, wherein the hot-rolled steel sheet has C, S, N, and Ti in a mass % satisfying the following (1) In the formula, C: 0.010% or more and 0.050% or less, Si: 0.2% or less, Mn: 0.10% or more, 0.80% or less, P: 0.025% or less, S: 0.01% or less, and N: 0.01. % or less, Al: 0.1% or less, Ti: 0.05% or more, 0.10% or less, and the remainder contains a composition of Fe and unavoidable impurities; the matrix of the ferrite grain iron phase with respect to the entire area of the structure is 95% or more. And a structure obtained by dispersing and depositing fine carbides containing Ti and having an average particle diameter of less than 10 nm; tensile strength is 590 MPa or more, Ti ^* /48<C/12 (1) Here, Ti ^* =Ti-(N/14×48+S/32×48) (C, S, N, Ti: content (% by mass) of each element). The high-tensile hot-rolled steel sheet according to the first aspect of the invention, in addition to the above-mentioned composition, further contains, in mass%, a formula of the following formula (2), and contains B: 0.0035% or less, B≧0.0003. -0.00025Mn (2) (Mn, B: content (% by mass) of each element). The high-tensile hot-rolled steel sheet according to the second aspect of the invention, wherein the B is 0.0003% or more and 0.0020% or less. The high-tensile hot-rolled steel sheet according to the first or second aspect of the invention, wherein the ratio of the number of precipitates Ps of the fine carbides to the number of random precipitates of the fine carbides satisfies the following ( 3) Formula: Pr/Ps ≧ 0.8 (2) (Pr: the number of fine carbides which are randomly deposited) (Ps: the number of fine carbides precipitated in a row). The high-tensile hot-rolled steel sheet according to the first or second aspect of the invention, wherein the volume ratio of the fine carbide to the entire structure is 0.0005 or more. The high-tensile hot-rolled steel sheet according to claim 5, wherein the volume ratio is 0.0005 or more and 0.003 or less. High-tension hot rolling as described in item 1 or 2 of the patent application scope The plated steel sheet contains, in addition to the above composition, Cu, Sn, Ni, Ca, Mg, Co, As, Cr, W, Nb, Mo, V, Pb, Ta in a total of 1% by mass or less. Any one or more. A method for producing a high-tensile hot-rolled steel sheet, comprising: performing hot rolling including rough rolling and finish rolling on a steel material, cooling and winding after completion of the finishing rolling to form a hot-rolled sheet, and then hot rolling The plate is sequentially subjected to a continuous annealing treatment and a plating treatment to form a hot-rolled steel sheet, and the steel material includes, in mass%, such that C, S, N, and Ti satisfy the following formula (1), and C: 0.010% or more and 0.050% or less, Si: 0.2% or less, Mn: 0.10% or more, 0.80% or less, P: 0.025% or less, S: 0.01% or less, N: 0.01% or less, and Al: 0.1% or less. Ti: 0.05% or more and 0.10% or less, and the remainder contains a composition of Fe and unavoidable impurities; the finish rolling temperature of the finish rolling is 880 ° C or higher, and the average cooling rate of the cooling is 10 ° C / s or more. The temperature of the winding is 400 ° C or more and less than 550 ° C, and the annealing temperature of the continuous annealing treatment is 550 ° C or higher and 750 ° C or lower, and the tensile strength is 590 MPa or more, Ti ^* /48 < C / 12 (1) Here, Ti ^* = Ti - (N / 14 × 48 + S / 32 × 48) (C, S, N, Ti: content of each element (% by mass)) . The method for producing a high-tensile hot-rolled steel sheet according to the eighth aspect of the invention, wherein, in addition to the above-described composition, the content of the following formula (2) is further satisfied by mass %, and B: 0.0035% or less is contained. B≧0.0003-0.00025Mn (2) (Mn, B: content (% by mass) of each element). The method for producing a high-tensile hot-rolled steel sheet according to claim 9, wherein the B is 0.0003% or more and 0.0020% or less. The method for producing a high-tensile hot-rolled steel sheet according to the sixth or seventh aspect of the invention, further comprising, in addition to the above composition, Cu, Sn, Ni, Ca in a total mass of 1% or less Any one or more of Mg, Co, As, Cr, W, Nb, Mo, V, Pb, and Ta.