JPH09143570A - Production of high tensile strength steel plate having extremely fine structure - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide a method for producing a high tensil strength hot rolled steel plate extremely excellent in ductility, toughness and fatigue strength. SOLUTION: A steel contg., by weight, 0.05 to 0.30% C, <=2.0% Si, 1.0 to 2.5% Mn and <=0.05% Al and contg. one or two kinds of 0.05 to 0.3% Ti and <=0.10% Nb, and the balance Fe with inevitable impurities is heated at 950 to 1100 deg.C, is thereafter applied with rolling reduction so as to regulated the draft to >=20% for at least >= two times and is subjected to hot rolling so as to regulate the finishing temp. to the Ar3 transformation point or above. After that, it is cooled in the temp. range of the Ar3 transformation point or above to 750 deg.C at a rate of >=20C/sec, is successively retained in the temp. range of <750 to 600 deg.C for 5 to 20sec, is again cooled to <=550 deg.C at a rate of >=20C/sec and is coiled round a coil at <=550 deg.C to obtain an extremely fine structure in which the ferrite volume rate is regulated to >=80% and the average ferrite grain size to <10μm.

Description

Detailed Description of the Invention

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing a high-strength hot-rolled steel sheet suitable for use in automobile materials, structural materials, pipe materials, etc., and particularly, it has ultrafine ferrite grains as hot-rolled. , A high-strength hot-rolled steel sheet having excellent ductility, toughness, and fatigue strength.

[0002]

2. Description of the Related Art In order to improve the mechanical properties of steel materials used for automobile materials, structural materials, pipe materials, etc., it is generally effective to refine the metal structure, and a manufacturing method aiming at an ultrafine structure. Has been sought after a lot.
Particularly in recent years, high-strength steel sheets have been widely used for cost reduction, and it is important to refine the structure of high-strength steel for the purpose of suppressing deterioration of ductility, toughness, durability ratio, etc. accompanying high tension. Has become a problem.

By the way, in order to miniaturize the structure, the methods conventionally used can be classified into a controlled cooling method, a large reduction rolling method, a controlled rolling method and the like. Among these manufacturing technologies, the precipitation-strengthened high-strength hot-rolled steel sheet obtained by applying the controlled rolling method to the steel containing Nb or Ti is the most promising method for simultaneously achieving high tensile strength and microstructure refinement. It has been widely used. The reason why this method was used is that precipitation strengthening action of Nb or Ti can easily achieve high tension, and the recrystallization suppressing action of austenite grains of Nb and Ti is utilized to obtain unrecrystallized austenite. This is because it is possible to obtain the effect of refining the ferrite crystal grains by promoting the γ → α strain-induced transformation when the grains are subjected to low-temperature rolling. However, a drawback of the high-strength hot-rolled steel sheet produced by this method is that the anisotropy of mechanical properties is large. For this reason, for example, in automotive steel sheets for press forming, the forming limit is governed by the characteristic level in the direction of the least ductility, so it is difficult to secure high pressability with steel sheets with large anisotropy. Become. Also in structural materials or pipe materials, if the anisotropy such as toughness and fatigue strength, which are important characteristics, is large, the same problem will occur.

On the other hand, as a structure refining method by large reduction rolling, for example, there is a proposal represented by JP-A-58-1238232. The main point of the refinement mechanism in these methods is that by applying a large reduction to the austenite grains,
→ It is to promote the strain-induced transformation to α.
It basically uses the same mechanism as the case of precipitation strengthened steel sheet containing Ti. However, the difference between the two is that in precipitation strengthened steel, Nb, it is necessary to utilize the recrystallization suppression effect of austenite grains of Ti, whereas in the large reduction rolling method of JP-A-58-1238232, Nb That is, it is possible to make the crystal grains fine without containing Ti. Therefore, there is an advantage that the anisotropy of mechanical properties is improved as compared with precipitation strengthened steel. However, the most difficult point of this method is that it is difficult to carry out with a general hot strip mill, such as a reduction amount of 40% or more per pass. Also,
Although a fine ferrite structure can be obtained by this method, it is also a drawback that it is difficult to achieve high strength at the same time.

[0005]

As described above, the conventional manufacturing method has various problems such as large anisotropy of mechanical properties, difficulty in obtaining high strength, and difficulty in actual operation.

An object of the present invention is to provide a manufacturing method which solves the problems of the above-mentioned known techniques, and more specifically, it can be easily carried out by a general hot strip mill and has different mechanical properties. It is an object of the present invention to provide a method for producing a high-strength hot-rolled steel sheet having a low degree of orientation. Further, an object of the present invention is to significantly enhance ductility, toughness and fatigue strength by further miniaturizing the ferrite crystal grain size as compared with the prior art in a high tensile strength, particularly in a high strength range of TS of 490 MPa or more. An object of the present invention is to provide a method for producing a high-strength hot-rolled steel sheet that can be manufactured.

[0007]

The present inventors avoid the above problems as long as the γ → α strain-induced transformation used as a means for refining the ferrite crystal grain size in the prior art is adopted. It was thought that it could not be achieved, and a new method of refining crystal grains was sought, and the present invention was completed. That is, the gist configuration of the present invention is as follows.

(1) C: 0.05 to 0.30 wt%, Si: 2.0 wt
% Or less, Mn: 1.0 to 2.5 wt%, Al: 0.05 wt% or less,
Steel containing at least one of Ti: 0.05 to 0.3 wt% and Nb: 0.10 wt% or less, with the balance consisting of Fe and inevitable impurities at a temperature of 950 to 1100 ° C. After heating, a reduction amount of 20% or more per time is applied at least twice, and hot rolling is performed so that the finishing temperature is the Ar ₃ transformation point or more, and the Ar ₃ transformation point to 750 ° C.
In the temperature range of less than 750 ° C to 600 ° C, 10 ° C /
After cooling at a rate of less than sec and staying for 5 to 20 seconds, it is cooled again to a temperature of 550 ° C or less at a rate of 20 ° C / sec or more and wound on a coil at a temperature of 550 ° C or less. A method for producing a high-strength hot-rolled steel sheet having an ultrafine structure having a ferrite volume ratio of 80% or more and an average ferrite grain size of less than 10 μm.

(2) C: 0.05 to 0.30 wt%, Si: 2.0 wt
% Or less, Mn: 1.0 to 2.5 wt%, Al: 0.05 wt% or less,
And one or two of Ti: 0.05 to 0.3 wt%, Nb: 0.10 wt% or less, and Cr: 1.5 wt% or less.
wt% or less, Cu: 1.5 wt% or less, Ni: 1.5 wt% or less,
Mo: A steel containing one or more selected from 1.5 wt% or less, the balance of which is Fe and unavoidable impurities, is heated to a temperature of 950 to 1100 ° C., and the reduction amount per time is 20. % or more and consisting reduction added at least twice, were hot rolled to finishing temperature becomes higher Ar ₃ transformation point, the temperature range of Ar ₃ transformation point to 750 ° C. 20 ° C. / sec
After cooling at the above rate, and subsequently in the temperature range of less than 750 ° C to 600 ° C, cooling at a rate of 10 ° C / sec or less, and allowing it to stay for 5 to 20 seconds, 20 ° C / se again.
Cool to a temperature of 550 ° C or less at a rate of c
The ferrite volume ratio is 80% or more, and the average ferrite grain size is 10%, which is characterized by being wound around a coil at a temperature of ℃ or less.
A method for producing a high-strength hot-rolled steel sheet having an ultrafine structure of less than μm.

[0010]

BEST MODE FOR CARRYING OUT THE INVENTION The grain refining method of the present invention is based on the combination of the following two means. The first means is to utilize recrystallization and the second means is to use controlled cooling after rolling.

First, the first means will be described in detail. It has long been known that there is a refinement process by rolling-recrystallization as a process in which austenite grains are refined in hot rolling. However, in general, the grain size of ferrite crystal that can be reached by such refining by recrystallization is at most 20 μm. On the other hand, according to the above-described controlled rolling method or large reduction rolling method, fine grains of about 10 μm can be obtained, so the refining method utilizing the recrystallization process is unsuitable as a means for obtaining an ultrafine structure. It has been thought that there is. However, the inventors have found that if the austenite grain size before the start of hot rolling, that is, the austenite grain size at the time of slab heating is extremely refined before rolling, the subsequent rolling-recrystallization is extremely accelerated. It was discovered that the refinement of recrystallized grains after rolling significantly progressed. The reason for this is not clear, but it is thought to be due to the mechanism described below.

Recrystallization of austenite grains by rolling includes dynamic recrystallization and static recrystallization. Of these, the former has a high reduction temperature, a low strain rate, and a large reduction, that is, a hot reduction. Generally speaking, hot rolling in a strip mill is a recrystallization that may occur only under rolling conditions corresponding to the initial to middle stages of rough rolling, and the rolling temperature decreases and strain rate It has been considered that this dynamic recrystallization becomes difficult to occur at the stage of finish rolling which becomes faster, and static recrystallization instead occurs.
By the way, dynamic recrystallization is a phenomenon in which strain is released by movement of grain boundaries or generation of new grain boundaries at an extremely high speed. The refinement of crystal grains facilitates the movement of grain boundaries, and thus acts in the direction of facilitating dynamic recrystallization. Also, since the nucleation of dynamic recrystallized grains is at the old grain boundary, the finer the older grains, the higher the frequency of nucleation of dynamic recrystallized grains, and the more refined the new grains after recrystallization should be Is. Thus, if the initial austenite grain size is extremely refined, dynamic recrystallization will occur even in the lower temperature region, the higher strain rate region, and the lower strain amount region, which could not occur in the conventional hot rolling. It is presumed that dynamic recrystallization will occur even in the finish rolling stage, and miniaturization due to dynamic recrystallization will progress as the number of reductions increases.

Needless to say, the most important point in the above-mentioned miniaturization mechanism is to extremely miniaturize the initial austenite grains in the slab heating stage. In the present invention, a means for this purpose is achieved by allowing a large amount of TiC to be present. Although Ti is used as a refining element also in the above-mentioned conventional precipitation-strengthened steel, the action of Ti in the present invention and that in precipitation-strengthened steel are clearly different. That is, the action of Ti in the conventional Ti-based precipitation-strengthened steel, the slab heating stage solutionized to austenite, to express the refining action by utilizing the recrystallization suppression effect as solid solution Ti, and transformed Re-precipitation as fine TiC in the subsequent ferrite grains to induce precipitation strengthening is included. Nb plays this role in Nb-based precipitation strengthened steel. Therefore, in precipitation strengthened steel, it is necessary to melt TiC or NbC in the slab heating stage, and it is essential that the heating temperature is relatively high. On the other hand, in the present invention, it is important that Ti is not dissolved in austenite in the slab heating stage and is present as TiC. This is because, firstly, solid solution Ti inhibits recrystallization and makes it difficult to cause dynamic recrystallization, which is the refinement process of the present invention. Secondly, the amount of TiC that suppresses the growth of initial austenite. Is reduced by its dissolution. Therefore, in the present invention, it is an essential requirement to set the slab heating temperature to a low temperature range where TiC melting does not occur.

Next, the controlled cooling which is the second miniaturization means in the present invention will be described. In many cases, the structure refining means by controlled cooling in the prior art has been used as a means for complementing it by combining it with a controlled rolling method or a large reduction rolling method. For example, Japanese Examined Patent Publication No. Sho 64-7131 is a typical example. The controlled cooling method in this proposal is "20 to 1000 ° C / sec after performing predetermined rolling.
At a cooling rate of less than 500 ° C. ”
The technical idea is based on the simple idea of quenching to a temperature range where the growth of ferrite crystal grains does not occur after rolling. On the other hand, the feature of the controlled cooling in the present invention is that the γ → α transformation region that occurs during cooling, that is, CC
In the temperature region near the ferrite nose in the T transformation curve, the rapid cooling is once stopped to provide a slow cooling period, and then the rapid cooling is performed again. The present inventors have found that by providing a slow cooling period within this predetermined temperature range during cooling, the refinement of the structure is further enhanced. The reason why such a phenomenon appears is speculated as follows. .

It is well known that the γ → α transformation proceeds by nucleation and growth, but when the final structure is mainly composed of ferrite as in the present invention, the ferrite grains are refined. It is considered that the number of ferrite nuclei formed is dominant as a factor that determines the degree.
The transformation region in which this nucleation occurs most actively is the region in which the ferrite transformation speed becomes the highest, and the CCT
It can be empirically understood that the vicinity of the ferrite nose in the curve is the corresponding region. As is clear from this, the significance of providing a slow cooling period in the vicinity of the ferrite nose is that the transformation proceeds in the temperature region in which the ferrite transformation nuclei are most actively generated, which allows the ferrite of the final structure to be formed. It is considered that grain refinement progresses. In addition, as an incidental effect, the two-phase (D
P) The structure and the residual γ structure are easily obtained, and there is an advantage that it can be used as a means for simultaneously achieving the refinement of the structure and the enhancement of the strength.

As described in detail above, the present invention provides a refinement technique by dynamic recrystallization of austenite grains by rolling,
It is possible to form ultrafine ferrite grains in a range that could not be achieved by conventional techniques by combining two techniques of controlled cooling technique that incorporates slow cooling in the ferrite nucleation region during the γ → α transformation. It was discovered and completed. Next, the reasons why the steel composition and manufacturing conditions in the present invention are set within the ranges shown in the above structural requirements will be described.

C: 0.05 to 0.30 wt% C is 0.05 in order to secure the strength and to secure a sufficient amount of TiC necessary in the heating stage to achieve the refinement of the structure.
wt% or more is required. However, if added in excess of 0.30 wt%, the proportion of the second phase increases, and the ductility and toughness deteriorate and the weldability also deteriorates. Therefore, C is
The range is 0.05 to 0.30 wt%, preferably 0.07 to 0.20 wt%.

Si: 2.0 wt% or less Si is an effective element for improving strength-stretch balance while improving strength-strength balance by solid solution strengthening, and promotes ferrite transformation to achieve a target of 80% or more ferrite. Although it is an element that exerts an effective action in obtaining a structure having a volume fraction, it is also an element that easily produces a scale with poor descaling property during hot rolling and tends to adversely affect the surface properties of the product. It is known that this adverse effect becomes more significant as the amount of Si increases and the heating temperature increases. In the present invention, since the heating temperature is set to a low temperature range for ultrafine structure, the upper limit of the amount of Si in which the surface properties are deteriorated as compared with ordinary steel can be made higher than that of ordinary steel, but 2.0 wt% When it exceeds, the adverse effect becomes apparent. Therefore, Si should be 2.0 wt% or less. The preferable content range is 0.3 to 1.6 wt%.

Mn: 1.0-2.5 wt% Mn is an essential element for affecting the transformation structure of the second phase and increasing the strength, and is required to be 1.0 wt% or more.
If it is added in excess of wt%, ferrite transformation will be delayed and it will be difficult to obtain a structure having a ferrite volume ratio of 80% or more, which is the aim of the present invention. Therefore, the amount of Mn added is 1.0 to 2.5.
wt%, preferably 1.2 to 2.0 wt%.

Al: 0.05 wt% or less Al is generally contained in the range of 0.010 to 0.10 wt% as a deoxidizing element.
In Al-killed steel, Al ₂ O ₃ generated by reoxidation of molten steel during casting into the mold causes nozzle clogging and deterioration of cleanliness due to mixing into the slab. For this reason, there is an adverse effect such that the means for improving productivity such as an increase in casting speed cannot be taken.
Such an adverse effect becomes particularly remarkable when Al exceeds 0.05 wt%. On the other hand, in the present invention, since it is premised that Si and Ti are added, the equilibrium oxygen content of the molten steel is sufficiently reduced by the addition of these elements. Less than that, rather, excessive addition of Al increases solid solution Al, and adverse effects such as inhibiting dynamic recrystallization of austenite grains appear. In order to avoid such a problem, the amount of Al needs to be 0.05 wt% or less, preferably 0.01 wt% or less.

Ti: 0.05 to 0.3 wt%, Nb: 0.10 wt% or less As described above, Ti is present as TiC to refine the initial austenite grains in the slab heating stage and to reduce the dynamics in the subsequent rolling process. It is an essential element to cause recrystallization. At least 0.05wt to exert this effect
% Or more, and the refinement effect becomes large with an increase in the TiC amount. However, even if added in excess of 0.3 wt%, it saturates, so the range is set to 0.05 to 0.3 wt%, preferably 0.07 to 0.20 wt%. The present invention is characterized in that the addition amount of Ti is relatively large as compared with the conventional precipitation strengthened steel and the like, but this has the following preferable effect in increasing the ferrite volume ratio. That is, since a part of C in the steel is fixed as TiC, C that forms the transformation second phase
The amount is reduced accordingly and the volume fraction of ferrite in the final microstructure is relatively high. This effectively contributes to the enhancement of ductility, low temperature toughness and fatigue properties as described later.

Further, Nb is an element having the same action as Ti in the present invention. A good effect can also be obtained by substituting Nb for Ti or by superposing it on Ti. However, the effect of Nb is almost equivalent to the effect of Ti when viewed in terms of atomic ratio equivalent to C, so that it is necessary to add approximately twice the weight ratio of Ti. Moreover, since it is an element that is more expensive than Ti at the present time, it has little economic advantage. However, in applications where welding such as ERW welding or flash butt welding is performed, the residual oxide at the welded joint interface may be a problem. In this case, it may be advantageous to use Nb instead of Ti. Nb may be added for such purposes and purposes. In this case, the effect of Nb is saturated when it exceeds 0.10, so 0.10 wt% or less is set.

In addition to the above basic components, Cr, Cu,
It is also possible to contain at least one of Ni and Mo. These elements bring about the same action as Mn,
Add as necessary to ensure the desired strength. Further, in addition to the strength, it has an action of enhancing, for example, weldability and corrosion resistance, so that it is effective to add it when improving these properties. However, these elements are more expensive than Mn, and if added excessively, both are economically disadvantageous, so the above elements are Cr: 1.5 wt% or less, Cu: 1.
5 wt% or less, Ni: 1.5 wt% or less, Mo: 1.5 wt% or less.

Heating Conditions In the present invention, it is a technically important point to maximize the effect of refining the initial austenite grains by TiC, and the conditions therefor are 950 to 110.
It is necessary to heat in the range of 0 ° C. That is, when the heating temperature exceeds 1100 ° C., the amount of TiC dissolved in austenite increases, the effect of refining the austenite grain size is lost, and the increase in solid solution Ti causes dynamic recrystallization during rolling. This is because it becomes difficult, and the desired high ferrite fraction and ultrafine ferrite grain size cannot be obtained, and only the mechanical properties similar to those of conventional hot-rolled steel sheets can be obtained. On the other hand, if the temperature is less than 950 ° C., it is difficult to finish the finish rolling in the austenite region, and it becomes difficult to secure the target microstructure and mechanical properties. The inventors of the present invention believe that the most preferable heating temperature range is obtained from the solubility product of Ti and C, and as a result of an experimental investigation, as a reference, the temperature (SRT) represented by the following formula (1) is + 20 ° C to- It was found to be in the range of 100 ° C. SRT (℃) =-10475 / [log {total Ti (%)-1.5S (%)-3.4N (%)}-5.33] +273 (1)

Hot Rolling Conditions In the present invention, the hot rolling causes the austenite grains to repeatedly undergo dynamic recrystallization to achieve the refinement. Since the initial conditions for inducing this dynamic recrystallization are ensured by satisfying the slab heating temperature requirement, the rolling reduction requirement is firstly an important factor. That is, if the reduction amount is less than 20%, the desired refinement by dynamic recrystallization will not be performed, so the lower limit of the reduction amount for each rolling stand is set to 20%.
The upper limit need not be particularly limited from the viewpoint of the refinement effect, but in reality, there is a limit due to the rolling capacity of the rolling mill,
Although it depends on the rolling temperature, the chemical composition of the steel, the rolling size, and the like, a rolling mill that can perform a reduction of 20 to 40% is common, and therefore it is easy to implement the requirements of the present invention.

Further, as the number of times of causing dynamic recrystallization increases, the refinement progresses. Therefore, the number of reductions until the finish rolling is important, and when the number of reductions is less than two, the purpose of the present invention is to It becomes impossible to obtain ultrafine ferrite particles of less than 10 μm. Therefore, the lower limit of the number of times of rolling is set to 2 times. Note that the total number of reductions during rolling in a normal hot strip mill is usually 10 to 12 passes in many cases, and the number of reductions is not insufficient. Of course, in order to carry out the present invention, it is not always necessary to carry out rolling in 10 to 12 passes, and for example, it is possible to carry out by carrying out omitting some reductions in the finish rolling mill or the rough rolling mill. Further, the finishing temperature must be higher than the Ar ₃ transformation point. This is because when hot rolling is completed at a low temperature below the Ar ₃ transformation point, excessive dislocations are introduced into the ferrite grains formed during hot rolling, and ductility and toughness deteriorate.

Cooling conditions The austenite grains that have been finish-rolled under the conditions according to the method of the present invention are substantially equiaxed fine grains, and γ →
Even if α-transformed, sufficiently fine ferrite grains can be obtained, but controlled cooling is performed on the run-out table in order to make the ferrite grains extremely fine. The control cooling consists of three stages of cooling sections, as described above. That is, the first stage is a temperature range in which the Ar ₃ transformation point after finish rolling to the frequency of occurrence of ferrite transformation nuclei is high, that is, 75
During the period of rapid cooling down to 0 ° C or less, the second stage is a temperature range in which ferrite transformation nuclei are actively generated (less than 750 ° C to 600
C.) for a predetermined time and then slowly cooled to increase the number of ferrite transformation nuclei. In the third step, the second phase that was present as the residual γ phase until the second step was hardened by pearlite, bainite or martensite. This is a quenching section for transforming into the second phase or remaining as the residual γ phase.

First, in the first-stage cooling, the cooling rate in the zone from the Ar ₃ transformation point to 750 ° C. after finish rolling is 20 ° C. /
Perform under the condition of sec. The reason for this is that the nucleation rate of the γ → α transformation that occurs at 750 ° C. or higher is small, and the progress of the γ → α transformation is mainly due to the grain growth of ferrite grains, so that the ferrite grain size tends to be large and the grain growth Due to γ
→ In order to prevent the α transformation, it is necessary to set the cooling rate in this section to 20 ° C / sec or more. The cooling rate in this section is 40 to 100 ° C / sec.
It is desirable to be within the range.

In the second stage cooling, less than 750 ° C. to 60 ° C.
The temperature range of 0 ° C. is cooled at a rate of 10 ° C./sec or less and allowed to stay in this temperature range for 5 to 20 seconds. The reason for this is γ → α
This is because the transformation can increase the number of ferrite transformation nuclei, which is more important for obtaining ultrafine ferrite grains, in the temperature range of less than 750 to 600 ° C. where the nucleation rate is high.
That is, if the temperature is 750 ° C. or higher or lower than 600 ° C., the rate of generation of ferrite nuclei is low, which is not preferable. It is to be noted that the more preferable temperature range is 700 to 650 ° C. The cooling rate in the above temperature range is 10 ° C / se
The reason for setting c or less is that it is a condition necessary for staying for 5 to 20 seconds without deviating from a favorable temperature range for nucleation. The reason why the residence time is 5 to 20 seconds is 5
This is because if it is less than 2 seconds, it is not sufficient to increase the ferrite transformation nucleus number and increase the ferrite volume fraction of the final structure to 80% or more of the target, and if it is retained for more than 20 seconds, it is aimed. This is because the effect will be saturated.
It is preferably 7 seconds or more in this range.

When the cooling conditions of the second stage are adopted, the residual γ phase which remains untransformed up to this stage also changes. This change is a phenomenon in which C discharged along with the transformation is concentrated in the residual γ phase. This phenomenon affects the transformation of the residual γ phase to the low temperature transformation phase that occurs in the third and subsequent steps, and when the C concentration is low, the low temperature transformation phase is likely to be pearlite or bainite, and when it is high, it is martensite. And the residual γ tends to remain. To obtain high-strength hot-rolled steel sheet, the concentration of C should be advanced and the lower temperature transformation
It is effective to generate a phase. Including such effects, the most desirable condition for the second stage slow cooling period is 7
It is better to be more than a second. A major feature of the controlled cooling in the present invention is that the slow cooling section of the second stage is adopted. By satisfying the requirements of the present invention, the effect of making the ferrite grains extremely fine and the ferrite volume ratio are increased. The effect and the effect of increasing the strength can be achieved at the same time.

In the third stage of cooling, cooling is performed at a rate of 20 ° C./sec or more to a temperature range of 550 ° C. or less. The requirement for this cooling is to remove residual γ phase from pearlite, bainite,
It is a necessary condition for forming a preferable second phase according to the purpose, such as transformation into a low temperature transformation phase such as martensite, or remaining until the end with residual γ.
Which of these low temperature transformation phases is used for the second phase is mainly selected depending on how much strength, workability or toughness is desired. It is better done by temperature. However, when the cooling rate in this section is less than 20 ° C / sec or the cooling stop temperature exceeds 550 ° C and becomes high, the low-temperature transformation phase has only a pearlite-based structure, resulting in higher strength. Even if the winding temperature is lowered to aim at bainite or martensite in order to achieve this, the aim cannot be achieved. The lower limit of cooling rate is 20 ° C / sec and the upper limit of cooling stop temperature is 5
The reason why the temperature is set to 50 ° C. is as described above.

Winding Conditions As described above, if the winding temperature is controlled within a predetermined range, the second phase is pearlite, bainite, martensite, residual γ depending on the target level of strength, ductility and toughness. Etc. can be adjusted to the organization. For example, when it is desired to suppress the strength relatively and increase the ductility, the winding temperature is set to be high and the second phase has a structure mainly composed of pearlite.
For a platform that requires high strength and low yield ratio material properties,
It is possible to set the winding temperature to a low temperature and make the second phase a structure mainly composed of martensite. However, when the winding temperature exceeds 550 ° C., the second phase cannot be made into martensite, the degree of freedom in adjusting the material becomes small, and the self-annealing effect after winding becomes large, resulting in an extremely high temperature. This causes unfavorable results such as grain growth of finely divided ferrite grains. Therefore, the upper limit of the winding temperature is 550 ° C. The desirable winding temperature range is 400 to 530 ° C.

[0033]

Next, the present invention will be described more specifically with reference to examples. Steel having the chemical composition shown in Table 1 was melted, hot-rolled and cooled under the conditions shown in Tables 2 and 3, and 3.0 mm
A hot-rolled steel sheet having a thickness is manufactured, and after being pickled, the polygonal ferrite volume ratio and the ferrite crystal grain size are measured,
Tensile properties by JIS No. 5 test piece, fatigue properties by both-way bending test method, and ductile-brittle transition temperature by 2 mm V notch Charpy test piece with the original thickness were investigated. The number of passes of 20% reduction or more in Tables 2 and 3 is the total number of passes with a reduction rate of 20% or more per pass. In any of the passes, the upper limit of the rolling reduction per pass was less than 40%. The results of these investigations are shown in Tables 4 and 5.

[0034]

[Table 1]

[0035]

[Table 2]

[0036]

[Table 3]

[0037]

[Table 4]

[0038]

[Table 5]

Based on the results of Tables 4 and 5, first, how the volume fraction of polygonal ferrite and the ferrite crystal grain size have an influence on the mechanical properties will be described. 1 and 2 are plots of the relationship between polygonal ferrite volume ratio or ferrite crystal grain size and TS × El, durability ratio (FL / TS), and vTrs based on the obtained data.

As is clear from these figures, all of the hot-rolled steel sheets according to the method of the present invention have a volume ratio of polygonal ferrite of 80% or more and a ferrite crystal grain size of less than 10 μm, and TS × is larger than that of the comparative example. It can be seen that the values of El, durability ratio, and vTrs are excellent. On the other hand, in the comparative example, most of the polygonal ferrite has a volume ratio of less than 80% and a ferrite crystal grain size of 10 μm or more.
o. No. 1, No. 27 and No. 29 with a polygonal ferrite volume ratio of 80% or more, and No. 12, No. 31 with a ferrite crystal grain size of less than 10 μm are included. The former group has a ferrite grain size of 1
The volume fraction of polygonal ferrite of the latter group is 0% or more and less than 80%.

These facts indicate that even if only one of the polygonal ferrite volume ratio and the ferrite crystal grain size can be adjusted within the range of the present invention, good mechanical properties cannot be obtained, and both conditions are satisfied. At the same time, it shows that good characteristics can be obtained only when the range of the present invention is satisfied.

[0042]

As described above, according to the manufacturing method of the present invention, the volume ratio of polygonal ferrite and the grain size of ferrite can be adjusted at the same time, whereby ductility, toughness, and
Fatigue strength can be remarkably increased. Further, according to the manufacturing method according to the present invention, since the volume ratio of polygonal ferrite is high, the anisotropy of mechanical properties is small, and
Since it can be easily carried out by a general hot strip mill, the industrial contribution is extremely large.

[Brief description of the drawings]

FIG. 1 is a graph showing the relationship between ferrite crystal grain size and mechanical properties.

FIG. 2 is a graph showing the relationship between polygonal ferrite volume ratio and mechanical properties.

─────────────────────────────────────────────────── ─── Continuation of the front page (51) Int.Cl. ⁶ Identification number Reference number within the agency FI Technical indication C22C 38/58 C22C 38/58 (72) Inventor Yoshio Yamazaki 1 Kawasaki-cho, Chuo-ku, Chiba-shi, Chiba Kawasaki Steel Co., Ltd. Technical Research Institute (72) Inventor Takashi Kobayashi 1 Kawasaki-cho, Chuo-ku, Chiba City, Chiba Prefecture Kawasaki Steel Co., Ltd. Technical Research Lab. Kawasaki Steel Corporation Technical Research Center

Claims (2)

[Claims] 1. C: 0.05 to 0.30 wt%, Si: 2.0 wt% or less, Mn: 1.0 to 2.5 wt%, Al: 0.05 wt% or less, and Ti: 0.05 to 0.3 wt%, Nb: 0.10. wt% or less, containing one or two of
A steel whose balance is Fe and unavoidable impurities is
After heating to a temperature of 1100 ° C, the reduction amount per operation is 2
A reduction of 0% or more is applied at least twice, hot rolling is performed so that the finishing temperature is the Ar ₃ transformation point or more, and the temperature range from the Ar ₃ transformation point to 750 ° C is cooled at a rate of 20 ° C / sec or more. Then, in the temperature range of less than 750 ° C to 600 ° C, the resin is allowed to stay for 5 to 20 seconds, and then again at 20 ° C /
Cool to a temperature of 550 ° C or less at a speed of sec or more, and
The ferrite volume ratio is 80% or more and the average ferrite grain size is 1 which is characterized by being wound around a coil at a temperature of 0 ° C or less.
A method for producing a high-strength hot-rolled steel sheet having an ultrafine structure of less than 0 μm. 2. C: 0.05 to 0.30 wt%, Si: 2.0 wt% or less, Mn: 1.0 to 2.5 wt%, Al: 0.05 wt% or less, and Ti: 0.05 to 0.3 wt%, Nb: 0.10. wt% or less, containing one or two of
Further, it contains one or more selected from Cr: 1.5 wt% or less, Cu: 1.5 wt% or less, Ni: 1.5 wt% or less, Mo: 1.5 wt% or less, and the balance is Fe and inevitable impurities. Steel, 9
After heating to a temperature of 50 to 1100 ° C., a reduction amount of 20% or more per time is added at least twice,
Hot rolling so that the finishing temperature is above the Ar ₃ transformation point,
After cooling in the temperature range of Ar ₃ transformation point to 750 ° C. at a rate of 20 ° C./sec or more, and then allowing it to stay for 5 to 20 sec in the temperature range of less than 750 ° C. to 600 ° C.
A pole having a ferrite volume ratio of 80% or more and an average ferrite grain size of less than 10 μm, characterized by being cooled to a temperature of 550 ° C. or lower at a rate of 0 ° C./sec or more and being wound around a coil at a temperature of 550 ° C. or less. A method for producing a high-strength hot-rolled steel sheet having a fine structure.