JP2011017044A - High-strength hot-rolled steel plate and manufacturing method therefor - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide a high-strength hot-rolled steel plate superior in formability for an extension flange, toughness and strength uniformity.SOLUTION: The high-strength hot-rolled steel plate includes 0.010-0.060% C, 0.5% or less Si, 0.8-1.8% Mn, 0.030% or less P, 0.01% or less S, 0.005-0.1% Al, 0.005% or less N, 0.035-0.100% Ti, and the balance Fe with unavoidable impurities. In the structure, polygonal ferrite having an average grain size of 5.0-10.0 μm occupies 80% or more by a fraction; the amount of Ti existing in precipitates with sizes of less than 20 nm is 70% or more of the value of Ti* calculated according to following expression (1): Ti*=[Ti]-48×[N]÷14 (1), wherein [Ti] and [N] represent component compositions (mass%) of Ti and N in the steel plate respectively; and the ratio of the amount of C precipitated as cementite with respect to the component composition (mass%) of C in the steel plate is 20% or less.

Description

  The present invention is useful for the use of skeletal members of large vehicles such as truck frames. The tensile strength (TS) is 540MPa or more and 780MPa or less, the strength variation in the coil is small, and stretch flangeability and toughness are excellent. The present invention relates to a high-strength hot-rolled steel sheet and a method for producing the same.

In recent years, in order to regulate CO ₂ emissions from the viewpoint of global environmental conservation, there is an urgent need to improve the fuel efficiency of automobiles, and there is a demand for weight reduction by using thinner materials. In addition, in order to ensure the safety of passengers in the event of a collision, safety improvements centering on the collision characteristics of automobile bodies are also required. For this reason, both weight reduction and strengthening of the automobile body are being actively promoted. It is said that it is effective to increase the strength of the member material in order to satisfy the weight reduction and strengthening of the automobile body at the same time. Recently, high-strength steel sheets are actively used for automobile parts. Since the weight reduction effect increases as the strength of the steel plate used increases, for example, there is a trend to use a steel plate having a tensile strength (TS) of 540 MPa or more as a skeleton member for large vehicles such as truck frames and construction machinery.

  On the other hand, many automobile parts made of steel plates are manufactured by press molding. Regarding the formability of a high-strength steel sheet, dimensional accuracy is important in addition to cracking and wrinkling, and in particular, control of the spring back is an important issue. Recently, CAE (Computer Assisted Engineering) has made the development of new cars more efficient, and it has become impossible to make molds many times. At the same time, when the characteristics of the steel plate are input, the amount of springback can be predicted with higher accuracy. However, when the variation of the springback amount is large, there arises a problem that the accuracy of prediction by CAE is lowered. Therefore, there is a demand for a high-strength steel sheet that is particularly excellent in strength uniformity with small strength variation.

  As a method for reducing the strength variation in the coil, Patent Document 1 discloses that after hot-rolling a precipitation-strengthened steel sheet bar to which Cu, Ni, Cr, and Mo are added and air-cooling for 1 second or longer, 450 A method is disclosed in which the coil has a strength variation in the longitudinal direction of the coil of ± 15 MPa or less by winding at a temperature in the range of ˜750 ° C. Patent Document 2 proposes a high-strength hot-rolled steel sheet excellent in strength uniformity with small strength variation in which very fine precipitates are uniformly dispersed by adding Ti and Mo in a composite manner. .

JP 2004-197119 A JP 2002-322541 A

However, the above prior art has the following problems.
The method described in Patent Document 1 is economically disadvantageous because Nb and Mo are added, resulting in an increase in cost. Furthermore, in steel sheets that aim to increase strength by adding Ti, V, and Nb, coarse precipitates are generated due to strain-induced precipitation when the steel sheet temperature is high after hot finish rolling. Therefore, there is a problem that an additional element is required excessively.
Further, although the steel sheet described in Patent Document 2 is Ti-based, expensive Mo needs to be added, resulting in an increase in cost.

  Furthermore, none of the patent documents considers the two-dimensional intensity uniformity in the coil plane including both the width direction and the longitudinal direction of the coil. Such intensity variation in the coil surface inevitably occurs because the coil cooling history after winding differs depending on the position, no matter how the winding temperature is controlled uniformly. In addition, stretch flangeability and toughness are not considered. Therefore, the conventional techniques have problems in processability and reliability with respect to characteristics under extremely low temperature environments.

  In view of such circumstances, the present invention advantageously solves the above problems, uses an inexpensive Ti-based general-purpose steel sheet without using expensive additive elements such as Ni, Nb, and Mo, and has a tensile strength (TS) of 540 MPa or more. An object of the present invention is to provide a high-strength hot-rolled steel sheet having a strength of 780 MPa or less, a small strength variation in the hot-rolled coil, and excellent strength uniformity having good stretch flangeability and toughness.

  After intensive studies to solve the above problems, the entire surface of the hot-rolled steel sheet was controlled by controlling the chemical composition of the steel sheet, the metal structure, the precipitation state of Ti contributing to precipitation strengthening, and the amount of C precipitated as cementite. In addition, the present invention was completed by successfully obtaining a high-strength hot-rolled steel sheet having a small strength variation over a wide range and having good stretch flangeability and toughness.

The summary of the high-strength hot-rolled steel sheet and the manufacturing method thereof according to the present invention is as follows.
[1] Component composition is mass%, C: 0.010 to 0.060%, Si: 0.5% or less, Mn: 0.8 to 1.8%, P: 0.030% or less, S: 0.01% or less, Al: 0.005 to 0.1%, N: 0.005% or less, Ti: 0.035 to 0.100%, the balance consisting of Fe and inevitable impurities, and the structure containing polygonal ferrite with an average particle size of 5.0 to 10.0 μm in a fraction of 80% or more The amount of Ti present in the precipitate having a size of less than 20 nm is 70% or more of the value of Ti * calculated by the following formula (1), and cementite with respect to the C component composition (mass%) of the steel sheet. A high-strength hot-rolled steel sheet characterized in that the proportion of the precipitated C is 20% or less.
Ti * = [Ti] −48 × [N] ÷ 14 ... (1)
Here, [Ti] and [N] indicate the component composition (mass%) of Ti and N of the steel sheet, respectively.
[2] Component composition is mass%, C: 0.010 to 0.060%, Si: 0.5% or less, Mn: 0.8 to 1.8%, P: 0.030% or less, S: 0.01% or less, Al: 0.005 to 0.1%, N: 0.005% or less, Ti: 0.035 to 0.100%, steel slab consisting of Fe and unavoidable impurities in the balance, heated to a heating temperature of 1200 to 1300 ° C, then hot at a finishing temperature of 800 to 950 ° C Perform finish rolling, start cooling at a cooling rate of 20 ° C./s or more within 2 seconds after the hot finish rolling, stop cooling at a temperature of 650 ° C. to 750 ° C., and continue for 2 to 30 seconds. A method for producing a high-strength hot-rolled steel sheet, which is subjected to a cooling step and then cooled again at a cooling rate of 100 ° C / s or more and wound at a temperature of 650 ° C or less.

In the present specification, “%” indicating the component of steel is “% by mass”. The high-strength hot-rolled steel sheet in the present invention is a steel sheet having a tensile strength (hereinafter sometimes referred to as TS) of 540 MPa or more and 780 MPa or less. Surface-treated steel sheets subjected to the above surface treatment are also targeted.
Further, the target characteristics of the present invention are that the intensity variation ΔTS in the hot-rolled coil is 35 MPa or less, the hole expansion value (λ) is 100% or more, and the energy transition temperature (Tr _E ) is −40 ° C. or less.

  According to the present invention, a high-strength hot-rolled steel sheet having a tensile strength (TS) of 540 MPa or more and 780 MPa or less, small variation in in-plane strength, and excellent stretch flangeability and toughness can be obtained. The high-strength hot-rolled steel sheet of the present invention can narrow the strength variation in the coil, thereby stabilizing the shape freezing property, part strength, and durability performance during press forming of the steel sheet. As a result, reliability in production and use as a steel plate for automobile parts, particularly large vehicles, is improved. Furthermore, in the present invention, the above effect can be obtained without adding an expensive raw material such as Nb, so that the cost can be reduced.

It is a figure which shows the result of having investigated the correlation with the fraction (%) of polygonal ferrite, and intensity variation (DELTA) TS (MPa). It is a figure which shows the result of having investigated the correlation with the particle size (micrometer) of polygonal ferrite, and intensity variation (DELTA) TS (MPa). FIG. 5 is a diagram showing the results of investigating the correlation between the proportion (%) of Ti contained in precipitates having a size of less than 20 nm with respect to Ti * and the intensity variation ΔTS (MPa). It is a figure which shows the result of having investigated the correlation with the ratio (%) of the amount of C which precipitated as cementite with respect to the component composition (mass%) of C of a steel plate, and a hole expansion value ((lambda)). C component composition of the steel sheet and the percentage of the amount of C precipitated as cementite for (mass%) (%) is a diagram showing the result of investigating the correlation between the energy transition temperature (Tr _E).

  The present invention is described in detail below.

First, an evaluation method for strength uniformity, that is, strength uniformity evaluation in the present invention will be described.
An example of the target steel sheet is a coil wound in a coil shape with a weight of 5 t or more and a steel sheet width of 500 mm or more. In such a case, in the state of hot rolling, the innermost and outermost windings at the front end and the rear end in the longitudinal direction and both ends 10 mm in the width direction are not evaluated. The strength variation (ΔTS) is evaluated with the distribution of tensile strength (TS) measured two-dimensionally on a sample which is divided into at least 10 parts in the longitudinal direction and at least 5 parts in the width direction. Further, the present invention is directed to the range where the tensile strength (TS) of the steel sheet is not less than 540 MPa and not more than 780 MPa.

  Next, the reason for limiting the chemical composition (component composition) of steel in the present invention will be described.

C: 0.010-0.060%
C is an important element in the present invention together with Ti described later. C forms a carbide with Ti and is effective for increasing the strength of the steel sheet by precipitation strengthening. In the present invention, 0.010% or more of C is contained from the viewpoint of precipitation strengthening. From the viewpoint of carbide precipitation efficiency, it is preferably 1.2 times or more of Ti * described later. On the other hand, excessively contained C precipitates as cementite. If it exceeds 0.060%, the toughness and hole expansibility are liable to be adversely affected, and the upper limit of the C content is 0.060%. A preferable range of the C content is 0.015 to 0.055%. The contained C is roughly divided into three patterns: (a) a solid solution state, (b) a state precipitated as TiC, and (c) a state precipitated as cementite (Fe ₃ C). In the steel of the present invention, (a) C in a solid solution state is 0.001%, and (b) the amount of C bonded to Ti is constant at 1.0 to 1.1 times as the atomic weight ratio of Ti *, so C: 0.010 to By setting the content in the range of 0.060%, the proportion of the amount of C precipitated as cementite can be made 20% or less. At this time, the upper limit of the C content is 2.5 times Ti * in terms of atomic weight ratio, that is, the weight ratio is 0.63 times Ti *.

Si: 0.5% or less
Si has the effect of improving ductility as well as the effect of solid solution strengthening. In order to acquire the said effect, it is preferable to contain Si 0.01% or more. On the other hand, when Si exceeds 0.5%, surface defects called red scale are likely to occur during hot rolling, which deteriorates the surface appearance of the steel sheet and adversely affects fatigue resistance and toughness. May have an effect. Therefore, the Si content is 0.5% or less. Preferably it is 0.05% or less.

Mn: 0.8-1.8%
Mn is effective for increasing the strength and has the effect of lowering the transformation point and refining the ferrite grain size, so it is necessary to contain Mn in an amount of 0.8% or more. Preferably it is 1.0% or more. On the other hand, if it contains excessive Mn exceeding 1.8%, a low-temperature transformation phase is generated after hot rolling and the ductility is lowered, and precipitation of Ti-based carbides described later tends to become unstable, resulting in a large variation in strength. Therefore, the upper limit of Mn content is 1.8%.

P: 0.030% or less P is an element effective for strengthening solid solution and has an effect of reducing scale defects caused by Si. However, if the P content exceeds 0.030%, P tends to segregate at grain boundaries, and toughness and weldability tend to deteriorate. Therefore, the upper limit of the P content is 0.030%.

S: 0.01% or less S is an impurity and exists as an inclusion in the steel, which significantly reduces the stretch flangeability and deteriorates various properties of the steel sheet such as causing hot cracking. There is a need to. Specifically, the S content is 0.01% or less because it is acceptable up to 0.01%. Preferably it is 0.005% or less.

Al: 0.005-0.1%
In addition to being useful as a deoxidizing element for steel, Al has the effect of fixing solute N present as an impurity and improving the normal temperature aging resistance. In order to exert such an effect, the Al content needs to be 0.005% or more. On the other hand, the content of Al exceeding 0.1% leads to a high alloy cost and further easily induces surface defects, so the upper limit of the Al content is set to 0.1%.

N: 0.005% or less N is an element that deteriorates normal temperature aging resistance, and is preferably an element that is preferably reduced as much as possible. Increasing N content degrades room temperature aging resistance and precipitates as coarse Ti-based nitride that contributes little to improving mechanical properties, so a large amount of Al or Ti is contained to fix solute N Is required. Therefore, it is preferable to reduce as much as possible, and the upper limit of the N content is 0.005%.

Ti: 0.035 to 0.100%
Ti is an important element for strengthening steel by precipitation strengthening. In the case of the present invention, it contributes to precipitation strengthening by forming carbide together with C.
In order to obtain a high-strength steel sheet having a tensile strength TS of 540 MPa or more and 780 MPa or less, it is preferable to refine the precipitate so that the precipitate size is less than 20 nm. It is also important to increase the proportion of this fine precipitate (precipitate size less than 20 nm). This is because when the size of the precipitate is 20 nm or more, it is difficult to obtain the effect of suppressing the movement of dislocations, and since the polygonal ferrite cannot be sufficiently hardened, the strength may be lowered. . Therefore, the size of the precipitate is preferably less than 20 nm. The precipitate containing fine Ti of less than 20 nm is formed by containing both Ti and C in the range of 0.035% to 0.100%.
In the present invention, these precipitates containing Ti and C are collectively referred to as Ti-based carbides. Examples of Ti-based carbides include TiC and Ti ₄ C ₂ S ₂ . Further, N may be included in the carbide as a composition, or may be precipitated in combination with MnS or the like.
Furthermore, in the high-strength steel sheet of the present invention, it has been confirmed that Ti-based carbides are mainly precipitated in polygonal ferrite. This is presumably because the solid solubility limit of C in polygonal ferrite is small, and thus supersaturated C tends to precipitate as carbide in polygonal ferrite. For this reason, such a precipitate hardens soft polygonal ferrite, and a tensile strength (TS) of 540 MPa or more and 780 MPa or less is obtained. At the same time, Ti is easily combined with solute N, and TiN is coarse and does not contribute to strengthening. Therefore, Ti is also a preferable element for fixing solute N. From this point of view, Ti is made 0.035% or more.
However, an excessive content of Ti is not preferable because it only produces TiC, which is a coarse undissolved carbide of Ti that does not contribute to strength in the heating stage, and is uneconomical. Therefore, the upper limit of Ti is 0.100%.
In the present invention, the balance other than the above-described components is composed of iron and inevitable impurities.

Next, the reason why the steel structure of the high-strength hot-rolled steel sheet of the present invention is limited will be described.
The amount of Ti present in the precipitate having a structure containing a polygonal ferrite having an average particle size of 5.0 to 10.0 μm in a fraction of 80% or more and having a size of less than 20 nm is calculated by the following equation (1). The ratio of the amount of C deposited as cementite with respect to the C component composition (mass%) of the steel sheet is 70% or more.
Ti * = [Ti] −48 × [N] ÷ 14 ... (1)
Here, [Ti] and [N] indicate the component composition (mass%) of Ti and N of the steel sheet, respectively.

  In conventional knowledge, the strength of the high-strength hot-rolled steel sheet according to the present invention is based on the strength of pure iron, solid solution strengthening, structure strengthening by cementite, grain refinement strengthening by grain boundaries, and fine Ti-based carbides This is determined by adding the four strengthening mechanisms of precipitation strengthening by. Of these, the basic strength is the strength inherent to iron, and the solid solution strengthening is almost uniquely determined once the chemical composition is determined. Therefore, these two strengthening mechanisms are hardly involved in the strength variation in the coil. The most closely related to the strength variation is the strengthening of structure, strengthening of fine particles, and strengthening of precipitation.

The amount of strengthening due to structure strengthening is determined by the chemical composition and the cooling history after rolling. The type of steel structure is determined by the temperature range that transforms from austenite, and once the steel structure is determined, the amount of strengthening is determined.
In the fine grain strengthening, as known by the Hall Petch rule, the grain interface area, that is, the grain size forming the steel structure and the strengthening amount have a correlation.
The amount of strengthening by precipitation strengthening is determined by the size and dispersion of the precipitate (specifically, the precipitate interval). Since the dispersion of the precipitate can be expressed by the amount and size of the precipitate, if the size and amount of the precipitate are determined, the strengthening amount by precipitation strengthening is determined.

Based on the above knowledge, next, an experiment was conducted to complete the present invention. The experimental facts that will serve as the basis for the invention will be described below.
Steel A shown in Table 1 whose chemical composition will be described later was melted in a converter and made into a slab by a continuous casting method. These steel slabs were reheated in the range of 1200 to 1300 ° C. and then roughly rolled to form sheet bars. This was subjected to finish rolling at a temperature of 800 to 950 ° C., and after 1.4 to 3.0 seconds from finish rolling, cooling was started at a cooling rate of 25 ° C./s or more, and cooling was stopped at a temperature of 550 to 780 ° C. Subsequently, after passing through a cooling process of 2 to 60 seconds, it is cooled again at a cooling rate of 50 to 200 ° C./s, wound in a temperature range of 700 ° C. or less, and a hot rolled steel sheet having a coil thickness of 6 to 14 mm. Manufactured. From the obtained hot-rolled steel sheet, 189 tensile test pieces were sampled in the same manner as the sampling position in Examples described later.

The correlation between the fraction (%) of polygonal ferrite and the strength variation ΔTS (MPa) was investigated for the hot-rolled steel sheet group produced as described above. The obtained results are shown in FIG. In FIG. 1, the vertical axis is strength variation ΔTS (MPa), the horizontal axis is the fraction of polygonal ferrite (%), the polygonal ferrite fraction is 80% or more with a symbol ○, and less than 80% with a symbol ×. Show.
From FIG. 1, it was found that the strength variation ΔTS showed a tendency to decrease as the polygonal ferrite fraction increased. When the polygonal ferrite fraction was 80% or more (symbol ◯), it was found that a sample group (region surrounded by a dotted line A in FIG. 1) having ΔTS of 35 MPa or less appeared.
The fraction of polygonal ferrite can be determined, for example, as follows. For the portion of the steel sheet excluding the 10% surface layer of the L section (cross section parallel to the rolling direction), the corrosion appearance structure by 5% nital is magnified 100 times with a scanning electron microscope (SEM). Smooth ferrite grains with grain boundary irregularities of less than 0.1 μm and no corrosion marks in the grains are defined as polygonal ferrite, and other forms of ferrite phases and different transformation phases such as pearlite and bainite Distinguish. These are color-coded on the image analysis software, and the area ratio is defined as the polygonal ferrite fraction.
On the other hand, the tensile test was performed in the same manner as in the examples described later. Further, the strength variation (ΔTS) was obtained by obtaining the standard deviation σ of the above-measured 189 points of tensile strength TS and multiplying this by four.

In response to the above results, next, those having a fraction of polygonal ferrite of 80% or more are extracted from the group of hot-rolled steel sheets produced as described above, and the grain diameter d _p (μm) of polygonal ferrite is extracted. And the correlation between intensity variation ΔTS (MPa). The obtained results are shown in FIG. In FIG. 2, the vertical axis is intensity variation ΔTS (MPa), the horizontal axis is the average grain diameter d _p (μm) of polygonal ferrite, and the average grain diameter of polygonal ferrite is 5.0 μm or more and 10.0 μm or less. Less than μm or more than 10.0 μm is indicated by a symbol x.
As shown in Fig. 2, a sample group (region surrounded by dotted line B in the figure) where ΔTS is 35 MPa or less appears in a part of the average ferrite ferrite grain size in the range of 5.0 µm to 10.0 µm (sign ○). I understand. However, when the plate thickness is less than 6 mm, the number of particle sizes existing in the plate thickness direction is relatively reduced, and even when the average particle size exceeds 10.0 μm, the strength variation is large enough to cause a problem as a whole steel material. It has been found that this is not possible. Moreover, in the steel plate with a large plate thickness, the cooling rate is high in the steel plate surface layer portion, but the cooling rate is lower in the plate thickness center portion than in the surface layer portion. In this case, if the polygonal ferrite grain size for the thickness suspension is not in the range of 5.0 μm to 10.0 μm, the grain size distribution in the thickness direction cannot be ignored. Therefore, when the plate thickness is 6 mm or more, the effect of the present invention can be further achieved if the average particle diameter is in the range of 5.0 μm to 10.0 μm.
The average grain size of polygonal ferrite was measured by a cutting method in accordance with JIS G 0551. For each photograph taken at a magnification of 100 times, three vertical and horizontal lines were drawn, and the average grain size was calculated. The average particle size was calculated to obtain the final particle size.
Further, the average particle diameter d _p of polygonal ferrite was a representative value with the values at the coil longitudinal center and width center.

In the steel of the present invention, when the metal structure is 80% or more of polygonal ferrite, Ti-based precipitates are deposited simultaneously with the progress of ferrite transformation. When these precipitates are coarsened, the strength is lowered, and the particle size distribution is wide and the strength variation is increased. Therefore, the particle size of the precipitate needs to be less than 20 nm that contributes to strengthening, and at this time, strength variation due to precipitation strengthening can be suppressed. In addition, since the contained C precipitates as a Ti-based precipitate, excessive hardening of the second phase (pearlite phase, martensite phase, bainite phase) can also be suppressed, and the fraction of the second phase is small. Variations can also be reduced.
Therefore, from the group of hot-rolled steel sheets manufactured as described above, the one having a polygonal ferrite fraction of 80% or more and the polygonal ferrite grain size of 5.0 μm or more and 10.0 μm or less is extracted. Correlation between the ratio [Ti ₂₀ ] / Ti * (%) of Ti amount [Ti ₂₀ ] contained in precipitates with a size less than 20 nm to Ti * expressed by the following formula (1) and the intensity variation ΔTS (MPa) investigated. The obtained results are shown in FIG. As described above, precipitates with a size of less than 20 nm that contribute to precipitation strengthening are formed by the contained Ti. Therefore, if the amount of Ti [Ti ₂₀ ] in the precipitates of less than 20 nm is grasped, Ti can be refined efficiently and finely. It is because it can be clarified whether it is deposited as a precipitate.
In FIG. 3, the vertical axis represents strength variation ΔTS (MPa), and the horizontal axis represents the ratio of Ti content in precipitates with a size less than 20 nm to Ti * [Ti ₂₀ ] / Ti * (%), and the size relative to Ti *. When the ratio [Ti ₂₀ ] / Ti * of the amount of Ti contained in the precipitates of less than 20 nm is 70% or more, it is indicated by a symbol ◯, and less than 70% is indicated by a symbol ×.
FIG. 3 shows that the intensity variation ΔTS tends to decrease as the ratio of Ti content [Ti ₂₀ ] / Ti * contained in precipitates of size less than 20 nm increases. It was also found that ΔTS was 35 MPa or less when the ratio [Ti ₂₀ ] / Ti * of the amount of Ti contained in precipitates of size less than 20 nm was 70% or more.
In addition, the ratio [Ti ₂₀ ] / Ti * of the amount of Ti contained in the precipitate having a size of less than 20 nm with respect to Ti * is a representative value with the values at the coil longitudinal center and width center.

From the above results, a steel structure containing polygonal ferrite in a fraction range of 80% or more, the particle size range of the polygonal ferrite is controlled to an average particle size of 5.0 μm to 10.0 μm, and a size of less than 20 nm It was conceived that if the amount of Ti contained in the precipitate was controlled so as to be in the range of 70% or more of Ti * represented by the following formula (1), the resulting strength variation ΔTS could be 35 MPa or less.
Ti * = [Ti] −48 × [N] ÷ 14 ... (1)
Here, [Ti] and [N] indicate the component composition (mass%) of Ti and N of the steel sheet, respectively.

  Therefore, the requirement of the present invention, that is, having a structure containing polygonal ferrite having an average particle diameter of 5.0 to 10.0 μm in a fraction of 80% or more, and being present in a precipitate having a size of less than 20 nm, If the amount is 70% or more of the value of Ti * calculated by the following formula (1) at any position of the hot rolled coil, the strength variation of the steel plate at each position is As a result, the entire steel sheet can be made excellent in strength uniformity with small strength variation.

The amount of Ti contained in the precipitate having a size of less than 20 nm can be measured by the following method.
After the sample is electrolyzed in a predetermined amount in the electrolytic solution, the sample piece is taken out of the electrolytic solution and immersed in a solution having dispersibility. Next, the precipitate contained in the solution is filtered using a filter having a pore diameter of 20 nm. Precipitates that have passed through the filter having a pore diameter of 20 nm together with the filtrate have a size of less than 20 nm. Next, the filtrate after filtration is analyzed by appropriately selecting from inductively coupled plasma (ICP) emission spectrometry, ICP mass spectrometry, atomic absorption spectrometry, etc., and precipitation with a steel composition size of less than 20 nm The amount of Ti in the object [Ti ₂₀ ] is obtained.

  Furthermore, it is another object of the present invention to obtain good stretch flangeability and toughness in addition to the above-described strength uniformity. As a result of the examination, it was found that the amount of cementite dominates the stretch flangeability and toughness. Therefore, next, in the steel A in Table 1, in a precipitate having a structure containing polygonal ferrite having an average particle size of 5.0 to 10.0 μm in a fraction of 80% or more and having a size of less than 20 nm. The ratio of the amount of C deposited as cementite to the C component composition (mass%) of the steel sheet for the sample where the amount of Ti present is 70% or more of the value of Ti * calculated by the following formula (1) The correlation between (%) and the hole expansion value (λ) was investigated. The obtained results are shown in FIG. The vertical axis is the hole expansion value (λ), and the horizontal axis is the ratio (%) of the amount of C deposited as cementite to the C component composition (mass%) of the steel sheet. Less than is indicated by a symbol x. FIG. 4 shows that the hole expansion value is 100% or more when the proportion (%) of C precipitated as cementite to the C component composition (mass%) of the steel sheet is 20% or less.

For the same sample as in FIG. 4, the correlation between the ratio (%) of the amount of C deposited as cementite to the C component composition (mass%) of the steel sheet and the energy transition temperature (Tr _E ) was investigated. The obtained results are shown in FIG. The vertical axis is the energy transition temperature (Tr _E ), the horizontal axis is the ratio (%) of the amount of C deposited as cementite to the C component composition (mass%) of the steel sheet, and the energy transition temperature is −40 ° C. or lower. The result of exceeding −40 ° C. is indicated by a symbol ×. Also in FIG. 5, as with the hole expansion value (λ) shown in FIG. 4, the energy transition temperature is 20% or less if the ratio (%) of C precipitated as cementite to the C composition (mass%) of the steel sheet However, it was found that good toughness of -40 ° C or lower can be obtained.
The measurement of the hole expansion value (λ) and the energy transition temperature (Tr _E ) was performed by the same method as in the examples described later.

  From the above, considering the strength uniformity, stretch flangeability, and toughness, it has a structure containing a polygonal ferrite having an average particle size of 5.0 to 10.0 μm in a fraction of 80% or more, and in a precipitate having a size of less than 20 nm. The amount of Ti present in the steel is 70% or more of the value of Ti * calculated by the following formula (1), and the ratio of the amount of C precipitated as cementite to the C component composition (mass%) of the steel sheet is 20%. It turned out that the steel plate which has the unprecedented favorable characteristic is obtained by setting it as the following.

Next, an example of a preferable method for producing the high-strength hot-rolled steel sheet of the present invention will be described.
The composition of the steel slab used in the production method of the present invention is the same as that of the steel sheet described above, and the reason for the limitation is also the same. The high-strength hot-rolled steel sheet of the present invention can be produced by using a steel slab having a composition within the above-described range as a raw material, and subjecting the raw material to rough rolling to obtain a hot-rolled steel sheet.

B) As one of the purposes of heating the steel slab at a heating temperature of 1200 ° C to 1300 ° C before hot rolling, the coarse Ti-based carbide produced before continuous casting is re-dissolved in the steel. Is mentioned. When the heating temperature is lower than 1200 ° C., the solid solution state of the precipitate becomes unstable, and the amount of fine Ti-based carbide generated in the subsequent process becomes non-uniform. Therefore, the lower limit of the heating temperature is 1200 ° C. On the other hand, heating exceeding 1300 ° C has an adverse effect of increasing scale loss on the slab surface, so the upper limit is set to 1300 ° C.
Next, the steel slab heated under the above conditions is subjected to hot rolling for rough rolling and finish rolling. Here, the steel slab is made into a sheet bar by rough rolling. The conditions for rough rolling need not be specified, and may be performed according to a conventional method. Further, from the viewpoint of securing the finish rolling temperature and preventing troubles during hot rolling, it is preferable to utilize a so-called sheet bar heater that heats the sheet bar.
Next, the sheet bar is finish-rolled to obtain a hot-rolled steel sheet.

B) Finishing temperature (FDT) of 800 ° C to 950 ° C
If the finishing temperature is less than 800 ° C, the rolling load increases, the rolling rate increases in the austenite non-recrystallization temperature region, abnormal texture develops, and coarse precipitates due to strain-induced precipitation of Ti-based carbides. Is not preferable. On the other hand, when the finishing temperature exceeds 950 ° C., the grain size of the polygonal ferrite is increased, and the formability is lowered or a scale defect is generated. Preferably it is set as 840 to 920 degreeC.
Moreover, in order to reduce the rolling load at the time of hot rolling, lubrication rolling may be performed between some or all passes of finish rolling. Lubricating rolling is effective from the viewpoint of uniform steel plate shape and uniform strength. The coefficient of friction during lubrication rolling is preferably in the range of 0.10 to 0.25. Furthermore, it is also preferable to set it as the continuous rolling process which joins the sheet bar which precedes and follows, and carries out finish rolling continuously. The application of the continuous rolling process is also desirable from the viewpoint of the operational stability of hot rolling.

C) Cooling is started at a cooling rate of 20 ° C / s or more (primary cooling) within 2 seconds after hot finish rolling, and cooling is started at a cooling rate of 20 ° C / s or more within 2 seconds after hot finish rolling. If the time exceeding 2 seconds elapses before starting cooling after finish rolling, the strain accumulated during finish rolling is released, resulting in coarsening of polygonal ferrite grains and strain-induced precipitation of coarse Ti-based carbides. It is not preferable. Moreover, the same phenomenon is likely to occur when the cooling rate is lower than 20 ° C./s.

D) Cooling is stopped in the temperature range of 650 ° C to 750 ° C, and then allowed to cool for 2 to 30 seconds.
Cooling is stopped at a temperature of 650 ° C. to 750 ° C., and then allowed to cool for 2 to 30 seconds. The cooling temperature should be a temperature at which Ti-based carbides such as TiC are effectively precipitated in a short time passing through the run-out table, and must be maintained for a certain period of time in the temperature range where the ferrite transformation proceeds most. At a cooling (holding) temperature of less than 650 ° C., the growth of polygonal ferrite grains is inhibited, and accordingly, precipitation of Ti carbide is less likely to occur. On the other hand, at a cooling (holding) temperature exceeding 750 ° C., it leads to an adverse effect of coarsening of polygonal ferrite grains and Ti-based carbide. Therefore, the cooling temperature is set to 650 ° C to 750 ° C.
In addition, the minimum cooling time for obtaining a polygonal ferrite fraction of 80% or more with the steel of the present invention is 2 seconds. In addition, when it is allowed to cool for more than 30 seconds, the strength decreases due to the coarsening of the Ti-based carbide. Therefore, the cooling time is 2 seconds to 30 seconds.

E) Cool again at a cooling rate of 100 ° C / s or higher (secondary cooling). Cool again at a cooling rate of 100 ° C / s or higher. In order to maintain the state of the fine Ti-based carbide stably obtained by the above-described process, a large cooling rate is required. Therefore, the lower limit of the cooling rate is 100 ° C / s.

F) Winding at a temperature of 650 ° C or less
Wind at a temperature of 650 ° C or lower. When the coiling temperature exceeds 650 ° C., the size of the precipitate becomes coarse and becomes extremely nonuniform. The lower limit of the winding temperature is not particularly defined because it does not cause a variation in strength with respect to the winding temperature on the low temperature side.

Next, examples of the present invention will be described.
Molten steel having the composition shown in Table 1 was melted in a converter and made into a slab by a continuous casting method. These steel slabs were heated at the conditions shown in Table 2, roughly rolled into sheet bars, and then hot-rolled steel sheets were formed by a hot rolling process in which finish rolling was performed under the conditions shown in Table 2.

These hot-rolled steel sheets were pickled, subjected to temper rolling with an elongation of 0.5%, and then trimmed and removed 10 mm in the end in the width direction to evaluate various properties. A steel sheet was collected from a dividing point obtained by dividing the innermost and outermost windings at the front end and the rear end in the longitudinal direction of the coil and the inside thereof into 20 equal parts in the longitudinal direction. Tensile specimens and precipitate analysis samples were collected from these width ends and dividing points divided into 8 in the width direction.

  Tensile test specimens were taken in the direction parallel to the rolling direction (L direction) and processed into JIS No. 5 tensile specimens. A tensile test was performed at a crosshead speed of 10 mm / min in accordance with the provisions of JIS Z 2241 to determine the tensile strength (TS).

  The hole-expansion test was conducted according to the iron standard JFST 1001.

  The toughness test was performed in accordance with JIS Z 2242. However, the notch shape of the test piece was V notch, and the test piece width was equal to the plate thickness.

  The microstructure of the L-section (cross section parallel to the rolling direction) of ± 17% of the center of the plate thickness was compared to 16 fields of view where the corrosion appearance structure by Nital was expanded 400 times with a scanning electron microscope (SEM). I went.

  The fraction of polygonal ferrite was determined as follows. For the portion of the steel sheet excluding the 10% surface layer of the L section (cross section parallel to the rolling direction), the corrosion appearance structure by 5% nital is magnified 100 times with a scanning electron microscope (SEM). Smooth ferrite grains with grain boundary irregularities of less than 0.1 μm and no corrosion marks in the grains are defined as polygonal ferrite, and other forms of ferrite phases and different transformation phases such as pearlite and bainite Distinguish. These are color-coded on the image analysis software, and the area ratio is defined as the polygonal ferrite fraction. The grain size of polygonal ferrite is a cutting method compliant with JIS G 0551. For one photograph taken at a magnification of 100, three vertical and horizontal lines are drawn to calculate the average grain size, and the average Was the final particle size.

The quantitative determination of Ti in the precipitate having a size of less than 20 nm was carried out by the following quantitative method.
The hot-rolled steel sheet obtained as described above is cut to an appropriate size, and about 0.2 g in a 10% AA electrolyte solution (10 vol% acetylacetone-1 mass% tetramethylammonium chloride-methanol) has a current density of 20 mA / cm ^2. And constant current electrolysis.
After the electrolysis, remove the sample piece with deposits on the surface from the electrolyte and immerse it in an aqueous solution of sodium hexametaphosphate (500 mg / l) (hereinafter referred to as the SHMP aqueous solution) to apply ultrasonic vibration. The precipitate was peeled off from the sample piece and extracted into an aqueous SHMP solution. Next, the SHMP aqueous solution containing the precipitate was filtered using a filter with a pore size of 20 nm, and the filtrate after filtration was analyzed using an ICP emission spectrometer, and the absolute amount of Ti in the filtrate was measured. . Next, the absolute amount of Ti was divided by the electrolytic weight to obtain the amount of Ti contained in the precipitate having a size of less than 20 nm (mass% when the total composition of the sample was 100 mass%). In addition, the electrolysis weight was calculated | required by measuring a weight with respect to the sample after deposit peeling, and subtracting from the sample weight before electrolysis. After this, the amount of Ti (mass%) contained in the precipitate having a size less than 20 nm obtained above was calculated by substituting the Ti and N contents shown in Table 1 into the formula (1). To obtain the ratio (%) of the amount of Ti contained in the precipitate having a size of less than 20 nm.
Ti * = [Ti] −48 × [N] ÷ 14 ... (1)
Here, [Ti] and [N] indicate the component composition (mass%) of Ti and N of the steel sheet, respectively.
The determined cementite was quantified by the following quantification method. The hot-rolled steel sheet obtained as described above is cut to an appropriate size, and about 0.5 g in a 10% AA-based electrolyte (10 vol% acetylacetone-1 mass% tetramethylammonium chloride-methanol) has a current density of 20 mA / cm ^2. And constant current electrolysis. The sample piece with the deposit on the surface after electrolysis was taken out from the electrolyte, immersed in the SHMP aqueous solution, applied with ultrasonic vibration, the precipitate was peeled off from the sample piece and extracted into the SHMP aqueous solution. . Next, the SHMP aqueous solution containing the precipitate was filtered using a filter having a pore size of 200 μm, and the extract obtained thereby was analyzed using an ICP emission spectroscopic analyzer, and the absolute amount of Fe was measured. Since the precipitate of Fe exists as cementite (Fe ₃ C), the amount of C precipitated as cementite is obtained from the measured amount of Fe, and the ratio of the amount of C precipitated as cementite is determined in the steel. From the C content of C and the amount of C precipitated as cementite.

  Table 3 shows the results of investigation of the tensile properties, hole expansion test, toughness test, microstructure, and precipitates of each hot-rolled steel sheet obtained as described above.

  Here, among the results shown in Table 3, polygonal ferrite fraction, particle size, ratio of Ti content in precipitates with a size of less than 20 nm to Ti * represented by formula (1), tensile strength TS, hole expansion test In the toughness test, the value at the center in the longitudinal direction and the center in the width of the coil is used as a representative value. The TS conformity ratio is a ratio at which the tensile strength TS showed a value of 540 MPa or more and 780 MPa or less among 189 points measured. ΔTS is obtained by obtaining the standard deviation σ at 189 TSs measured per sample and multiplying this by four.

As is clear from the investigation results shown in Table 3, in all of the examples of the present invention, TS has a high strength of 540 MPa or more, and the strength variation (ΔTS) in the coil surface is as small as 35 MPa or less, and the strength is uniform. A good steel sheet is obtained. Furthermore, the TS conformance ratio is closely related to the amount of fine precipitates, and the TS conformance ratio is higher as the ratio of the amount of Ti contained in precipitates having a size of less than 20 nm is larger. Further, the hole expansion value (λ) is 100% or more and the energy transition temperature (Tr _E ) is −40 ° C. or less, which shows that the stretch flangeability and toughness are excellent.
Further, from these results, in the present invention, in particular, the strength variation ΔTS in a hot-rolled coil having a plate thickness of 6 mm or more and 14 mm or less can be set to 35 MPa or less. It becomes possible to stabilize the shape freezing property, member strength, and durability performance.

  The high-strength hot-rolled steel sheet of the present invention has a tensile strength (TS) of 540 MPa or more and 780 MPa or less, small strength variation, and excellent stretch flangeability and toughness. Therefore, for example, when the high-strength hot-rolled steel sheet of the present invention is applied to automobile parts, variations in springback amount and collision characteristics after forming in high tension can be reduced, and the vehicle body design can be made highly accurate. It can contribute to collision safety and weight reduction.

Claims (2)

Component composition is mass%, C: 0.010-0.060%, Si: 0.5% or less, Mn: 0.8-1.8%, P: 0.030% or less, S: 0.01% or less, Al: 0.005-0.1%, N: 0.005 % Or less, containing Ti: 0.035 to 0.100%, the balance being Fe and inevitable impurities, having a structure containing polygonal ferrite having an average particle size of 5.0 to 10.0 μm in a fraction of 80% or more, The amount of Ti present in the precipitate having a size of less than 20 nm is 70% or more of the value of Ti * calculated by the following formula (1), and precipitated as cementite with respect to the C component composition (mass%) of the steel sheet. A high-strength hot-rolled steel sheet characterized by a C content ratio of 20% or less.
Ti * = [Ti] −48 × [N] ÷ 14 ... (1)
Here, [Ti] and [N] indicate the component composition (mass%) of Ti and N of the steel sheet, respectively.   Component composition is mass%, C: 0.010-0.060%, Si: 0.5% or less, Mn: 0.8-1.8%, P: 0.030% or less, S: 0.01% or less, Al: 0.005-0.1%, N: 0.005 % Steel, Ti: 0.035 to 0.100%, the remainder of the steel slab consisting of Fe and inevitable impurities is heated to a heating temperature of 1200 ° C to 1300 ° C and then hot finished at a finishing temperature of 800 ° C to 950 ° C Rolling is started, cooling is started at a cooling rate of 20 ° C./s or more within 2 seconds after the hot finish rolling, the cooling is stopped at a temperature of 650 ° C. to 750 ° C., and then released for 2 seconds to 30 seconds. A method for producing a high-strength hot-rolled steel sheet, which is subjected to cooling at a cooling rate of 100 ° C./s or higher and wound at a temperature of 650 ° C. or lower after the cooling step.

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