JP2005232483A - High-strength steel sheet having superior deep drawability and balance of strength and ductility, and manufacturing method therefor - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a high-strength steel sheet having superior deep drawability and a superior balance of strength and ductility, and to provide a manufacturing method therefor. <P>SOLUTION: The high-strength steel sheet has a component composition comprising, by mass%, 0.010-0.050% C, 0.01-1.0% Si, 1.0-3.0% Mn, 0.005-0.1% P, 0.01% or less S, 0.005-0.1% Al, 0.01% or less N, 0.03-0.3% Nb, so that the contents of N and C can satisfy a relationship of 0.2≤(Nb/93)/(C/12)≤0.7 (where Nb and C represent the contents of each element(mass%)), and the balance substantially Fe with unavoidable impurities; and has a steel structure including 50% or more of a ferrite phase by an area rate, and 1% or more of a martensite phase by an area rate; has an average of an r-value of 1.2 or higher; and the product (TS×El) of tensile strength (TS) and elongation (El) in an amount of 19,000 MPa×% or more. <P>COPYRIGHT: (C)2005,JPO&NCIPI

Description

  The present invention is useful for the use of automobile steel sheets and the like, and has a high tensile strength (TS) of 440 MPa or more and a high r value (r value ≧ 1.2), and has a tensile strength (TS) and elongation (El ) Product (TS × El) is 19000 MPa ·% or more and is intended to propose a high-strength steel sheet excellent in deep drawability and strength-ductility balance and its manufacturing method.

In recent years, in order to regulate CO ₂ emissions from the viewpoint of global environmental conservation, improvement in fuel efficiency of automobiles has been demanded. In addition, in order to ensure the safety of passengers in the event of a collision, it is also required to improve safety centered on the collision characteristics of the automobile body. As described above, the weight reduction of the automobile body and the reinforcement of the automobile body are being actively promoted.

  In order to satisfy the weight reduction and strengthening of automobile bodies at the same time, it is said that it is effective to reduce the thickness by reducing the plate thickness by increasing the strength of the component material within a range where rigidity does not become a problem. Steel plates are actively used in automotive parts.

  Since the weight reduction effect increases as the strength of the steel sheet used increases, the automotive industry tends to use a steel sheet having a tensile strength (TS) of 440 MPa or more as a panel material for inner and outer plates, for example.

  On the other hand, since many automotive parts made of steel plates are formed by press working, the steel plates for automobiles are required to have excellent press formability. However, since high-strength steel sheets are greatly deteriorated in formability, especially deep drawability, compared with ordinary mild steel sheets, TS ≧ 440 MPa, more preferably TS ≧ 500 MPa, is an issue in promoting automobile weight reduction. In addition, there is an increasing demand for steel sheets that have good deep drawability, and high strength steel sheets with an average r value ≥ 1.2 at the Rankford value (hereinafter referred to as "r value"), which is an evaluation index of deep drawability, are required. Has been.

As a means to increase strength while having a high r value, based on steel that has been converted to IF (Interstitial Free) by adding an amount of Ti, Nb solute carbon and solute nitrogen fixed to an extremely low carbon steel sheet, For example, there is a method of adding a solid solution strengthening element such as Si, Mn, and P. For example, there is a method disclosed in Patent Document 1.
JP-A-56-139654

Patent Document 1 has a composition of C: 0.002 to 0.015%, Nb: C% × 3 to C% × 8 + 0.020%, Si: 1.2%, Mn: 0.04 to 0.8%, P: 0.03 to 0.10%. This is a technology related to a high-tensile cold-rolled steel sheet having a non-aging property of a tensile strength of 35 to 45 kg / mm class ² (340 to 440 MPa class) and excellent formability.

  However, in such a technology using ultra-low carbon steel as a raw material, when trying to produce a steel sheet with a tensile strength of ≧ 440 MPa, the amount of added alloying elements increases, resulting in surface appearance problems, plating deterioration, It has been found that problems such as the manifestation of the next processing brittleness arise. In addition, when a solid solution strengthening component is added in a large amount, the r value deteriorates, so there is a problem that the level of the r value decreases as the strength increases.

In addition, in order to reduce the C content to an extremely low carbon range, vacuum degassing must be performed in the steelmaking process, that is, this generates a large amount of CO ₂ during the manufacturing process, which is a viewpoint of global environmental conservation. It is hard to say that it is the most suitable.

  In addition to the solid solution strengthening as described above, there is a structure strengthening method as a method for increasing the strength of a steel sheet. For example, there is a DP (Dual-Phase) steel sheet which is a composite structure steel sheet composed of a soft ferrite phase and a hard martensite phase. DP steel is generally good in ductility, has an excellent strength-ductility balance (TS x El), and has a low yield ratio, that is, a low yield stress for its tensile strength. There is a feature that the shape freezing property at the time is excellent, but the r value is low and the deep drawability is inferior. This is because, in addition to the presence of a martensite phase that does not contribute to the r value in terms of crystal orientation, the solid solution C essential for martensite formation forms a {111} recrystallized texture effective for increasing the r value. It is said to inhibit.

As an attempt to improve the r value of such a composite structure steel plate, for example, there is a technique of Patent Document 2 or Patent Document 3.
Japanese Patent Publication No.55-10650 JP-A-55-100934

In the technique of Patent Document 2, after cold rolling, box annealing is performed at a temperature of the recrystallization temperature to the Ac ₃ transformation point, and then heating to 700 to 800 ° C. to obtain a composite structure, followed by quenching and tempering. Is disclosed. However, in this method, since the quenching and tempering is performed during the continuous annealing, the manufacturing cost becomes a problem. In the case of box annealing, it is inferior to continuous annealing in terms of processing time and efficiency.

  In the technique of Patent Document 3, after cold rolling in order to obtain a high r value, box tempering is first performed, and the temperature at this time is set to a two-phase region of ferrite (α) phase-austenite (γ) phase. Continuous annealing is performed. In this technique, Mn is concentrated from the α phase to the γ phase during soaking of the box annealing. This Mn-concentrated phase preferentially becomes a γ phase during the subsequent continuous annealing, and a mixed structure can be obtained even at a cooling rate of the order of a gas jet. However, this method requires a long annealing time at a relatively high temperature for Mn concentration. Therefore, there are many problems in the manufacturing process such as frequent adhesion between steel plates, generation of temper collar, and reduction in the life of the furnace inner cover. There's a problem.

In Patent Document 4, C: 0.003 to 0.03%, Si: 0.2 to 1%, Mn: 0.3 to 1.5%, Ti: 0.02 to 0.2% (however, the atomic concentration ratio of (effective Ti) / (C + N) is 0.4). -0.8) Composite structure type high tension excellent in deep drawability and shape freezing property, characterized by hot rolling, cold rolling, and continuous annealing that is rapidly cooled after heating to a predetermined temperature It is a manufacturing method of a cold-rolled steel plate. In this technology, a steel having a composition of 0.012% C-0.32% Si-0.53% Mn-0.03% P-0.051% Ti is heated to 870 ° C which is a two-phase region of α-γ after cold rolling. Thereafter, a technique is disclosed in which a composite structure cold-rolled steel sheet having an r value = 1.61 and TS = 482 MPa can be manufactured by cooling at an average cooling rate of 100 ° C./s. However, in order to obtain a high cooling rate of 100 ° C / s, water quenching equipment is required, and water-quenched steel plates have surface treatment problems, so there are problems with manufacturing equipment and materials. is there.
Japanese Patent Publication No. 1-35900

Furthermore, Patent Document 5 discloses a technique for improving the r value of a composite steel sheet by optimizing the V content in relation to the C content. This is because before recrystallization annealing, C in the steel is precipitated with V-based carbides to reduce the solute C as much as possible to achieve a high r value, and subsequently heated in the two-phase region of α-γ to make V-based carbides. Is dissolved, C is concentrated in γ, and a martensite phase is generated in the subsequent cooling process. However, the addition of V causes an increase in alloy cost because it is an expensive element, and further, VC precipitated in the hot-rolled sheet increases the deformation resistance during cold rolling. % Cold rolling increases the load on the roll, increases the risk of trouble occurrence, and has a manufacturing problem such as concern about a decrease in productivity.
Japanese Patent Laid-Open No. 2002-226941

Moreover, there exists a technique of patent document 6 as a technique of the high strength steel plate excellent in deep drawability, and its manufacturing method. This technique obtains a high-strength steel sheet containing a predetermined amount of C, having an average r value of 1.3 or more, and having a total of 3% or more of one or more of bainite phase, martensite phase, and austenite phase in the structure. As its manufacturing method, the rolling reduction of cold rolling is set to 30 to 95%, and then the texture is developed to form a cluster and precipitates of Al and N to increase the r value. Subsequently, heat treatment is carried out so as to have a total of 3% or more of one or more of the bainite phase, martensite phase, and austenite phase in the structure. In this method, after cold rolling, annealing for obtaining a good r value and heat treatment for forming a structure are required, respectively, and further, the annealing process requires a long holding time of 1 hour or more. Therefore, there is a problem that productivity is poor in terms of process (time). Furthermore, the second phase fraction of the resulting structure is relatively high, which makes it difficult to stably secure an excellent strength-ductility balance.
JP 2003-64444 A

  In order to increase the strength of a (soft) steel sheet with excellent deep drawability, the conventional methods for increasing the strength by solid solution strengthening require the addition of a large amount or an excessive amount of alloy components, which is costly. Both in terms of process, process and r-value improvement. In addition, the method using structural strengthening requires a two-time annealing (heating) method and a high-speed cooling facility, and there are problems in the manufacturing process. Further, a method using VC is disclosed, but V is expensive. In addition to increasing the alloy cost, precipitation of VC increases deformation resistance during rolling, which also makes stable production difficult.

  An object of the present invention is to propose a high-strength steel sheet having a good deep drawability and a good balance between strength and ductility, and a method for producing the same, which have advantageously solved the problems of the prior art.

The present invention has been intensively studied to solve the above-mentioned problems. As a result, the C content is within a C content range of 0.01 to 0.05% without using special or excessive alloy components or equipment. By regulating the Nb content, the average r value is 1.2 or more, TS x El
However, it has succeeded in obtaining a high-strength steel sheet having a steel structure containing a ferrite phase and a martensite phase with an excellent deep drawability and strength-ductility balance at 19000 MPa ·% or more.

The gist of the present invention is as follows.
(1) In mass%,
C: 0.010 to 0.050%
Si: 0.01 to 1.0%
Mn: 1.0-3.0%
P: 0.005-0.1%
S: 0.01% or less,
Al: 0.005-0.1%
N: 0.01% or less and
Nb: 0.03-0.3%
And Nb content and C content are 0.2 ≦ (Nb / 93) / (C / 12) ≦ 0.7 (Nb and C in the formula are the contents (mass%) of each element) The relationship is satisfied, and the balance has a steel composition containing a component composition consisting essentially of Fe and inevitable impurities, and including a ferrite phase with an area ratio of 50% or more and a martensite phase with an area ratio of 1% or more. The average r value is 1.2 or more, and the product of tensile strength (TS) and elongation (El) (TS × El) is 19000 MPa ·% or more. Excellent high strength steel plate.

(2) The high-strength steel sheet excellent in deep drawability and strength-ductility balance as described in (1) above, further containing Mo: 0.5% or less by mass% in addition to the above composition.

(3) In addition to the above composition, Ti: 0.1% by mass or less is further contained, and the contents of Ti, S and N in the steel are (Ti / 48) / {(S / 32) + (N / 14)} ≦ 2 (wherein Ti, S and N are the contents (mass%) of each element) satisfying the relationship of (1) or (2) High-strength steel sheet with excellent deep drawability and strength-ductility balance.

(4) The high-strength steel sheet excellent in deep drawability and strength-ductility balance according to any one of (1) to (3) above, wherein the surface has a plating layer.

(5) By mass%
C: 0.010 to 0.050%
Si: 0.01 to 1.0%
Mn: 1.0-3.0%
P: 0.005-0.1%
S: 0.01% or less,
Al: 0.005-0.1%
N: 0.01% or less and
Nb: 0.03-0.3%
And Nb and C content (mass%) is 0.2 ≦ (Nb / 93) / (C / 12) ≦ 0.7 (where Nb and C are the contents of each element (mass%) )) When the steel slab having a composition satisfying the above) is hot-rolled and the finish rolling exit temperature is FT (° C.) and the final rolling reduction of the final three stands is X (%), the finish rolling exit The temperature FT is 800 ≦ FT ≦ 800 + 25 × X × Nb (where Nb is the Nb content (mass%) in the steel) and is subjected to finish rolling, and 25 ° C./s within 0.5 seconds after the finish rolling A cold rolling process in which the steel sheet is cooled and rolled at a coiling temperature of 500 to 720 ° C. to be a hot rolled sheet, and the hot rolled sheet is pickled and cold rolled to form a cold rolled sheet. The cold rolled sheet is annealed at an annealing temperature of 800 to 950 ° C., and then cooled at an average cooling rate of 5 ° C./s or more in the temperature range from the annealing temperature to 500 ° C. Characterized by sequential application To deep drawability and strength - the method of producing a high strength steel sheet excellent in ductility balance.

(6) The steel slab further contains Mo: 0.5% or less by mass% in addition to the above composition. The high-strength steel sheet excellent in deep drawability and strength-ductility balance described in (5) above Production method.

(7) In addition to the above composition, the steel slab further contains Ti: 0.1% or less by mass%, and the content of Ti, S and N in the steel is (Ti / 48) / {(S / 32) Deep drawing according to the above (5) or (6) satisfying the relationship of + (N / 14)} ≦ 2 (wherein Ti, S and N are the contents (mass%) of each element) Of high-strength steel sheet with excellent balance between strength and strength-ductility.

(8) Deep drawability and strength-ductility, characterized in that in the manufacturing method according to any one of (5) to (7) above, a squeezing treatment is performed after the cold-rolled sheet annealing step. A method for producing high-strength steel sheets with excellent balance.

  This invention is necessary for the formation of martensite when the C content is in the range of 0.010 to 0.050 mass% without thoroughly reducing solute C, which has an adverse effect on deep drawability, unlike conventional ultra-low carbon IF steels. The {111} recrystallized texture is developed in spite of the state in which the solid solution C remains, and the average r value ≧ 1.2 is secured to provide a good deep drawability. By forming a composite structure having a phase and a second phase containing a martensite phase, high strength of TS ≧ 440 MPa, more preferably TS ≧ 500 MPa is achieved.

The reason for this is not necessarily clear, but it is thought to be as follows.
In order to increase the r value, that is, to develop a {111} recrystallized texture, in conventional mild steel sheets, it is possible to reduce the solute C before cold rolling and recrystallization as much as possible, It has been regarded as an effective means. On the other hand, in the DP steel plate as described above, since the solute C necessary for the formation of the martensite phase is required, the recrystallization texture of the parent phase does not develop and the r value is low. However, in the present invention, it has been newly found that there is an exquisite component range that enables both the development of {111} recrystallized texture and the formation of martensite phase. That is, in addition to the C content of 0.010 to 0.050% by mass, the C content is lower than that of the conventional DP steel sheet (low carbon steel level), however, the C content is higher than that of the ultra low carbon steel. It was newly found that both the development of {111} recrystallization texture and the formation of martensite phase can be performed by adding Nb appropriately.

  As conventionally known, Nb has a recrystallization delay effect, so it is possible to refine the hot-rolled sheet structure by appropriately controlling the finishing temperature during hot rolling. In Nb, Nb has a high carbide forming ability.

  Especially in the present invention, in addition to refining the hot-rolled sheet structure by setting the finish rolling outlet temperature to an appropriate range in relation to the total rolling reduction and Nb content of the final three stands of finish rolling, the coil after hot rolling By making the coiling temperature appropriate, the hot-rolled sheet is made uniform and refined, and NbC is precipitated in the hot-rolled sheet to reduce the solute C before cold rolling and before recrystallization. . Here, the ratio of Nb to the amount of C is 0.2 ≦ (Nb / 93) / (C / 12) ≦ 0.7 (Nb and C in the formula are the contents of each element (mass%)). That is, by setting the Nb amount to Nb / C (atomic ratio) = 0.2 to 0.7 in terms of the atomic ratio with respect to the C amount, C that does not precipitate as NbC is present. Conventionally, it has been said that the presence of such C inhibits the development of {111} recrystallized texture, but in the present invention, all C is not precipitated and fixed as NbC, and solid solution C necessary for the formation of the martensite phase is not present. High r value can be achieved while existing. The reason for this is not clear, but rather than a negative factor for the formation of {111} recrystallized texture due to the presence of solute C, in addition to refinement of the hot rolled sheet structure, fine NbC is precipitated in the matrix. This is thought to be due to the large positive factor that accumulates strain near the grain boundary during cold rolling and promotes the generation of {111} recrystallized grains from the grain boundary. In particular, the effect of precipitating NbC in the matrix is not effective at the C content of the conventional ultra-low carbon steel, and is presumed to exhibit the effect for the first time at the C content level of the present invention. Finding this area is the basis of the technical idea of the present invention. C other than NbC and its existence form are presumed to be cementite-based carbides or solute C, but the presence of C that was not fixed as NbC caused the formation of martensite phase during cooling in the annealing process. It was possible to achieve high strength.

  According to this manufacturing method, compared with the prior art, a degassing step for making an ultra-low carbon steel is not necessary in the steel making process, and addition of an excessive alloy element is not required for utilizing solid solution strengthening. This is also advantageous in terms of cost. Furthermore, the addition of V as in the technique disclosed in Patent Document 5 increases the deformation resistance during rolling, increases the load on the roll, and is generally effective for increasing the r value. In order to obtain the above, there is a problem that the risk of trouble increases and the productivity may be lowered, but the present invention does not have such a concern.

The present invention is described in detail below.
The content of the element in the steel is mass%, but hereinafter, it is simply expressed as% unless otherwise specified.
First, the reason which limited the component composition of the steel plate of this invention is demonstrated.

・ C: 0.010 to 0.050%
C is an important element in the present invention together with Nb described later. C is effective in increasing the strength and promotes the formation of a composite structure having a ferrite phase as a main phase and a second phase including a martensite phase. Therefore, in the present invention, C is contained in an amount of 0.010% or more from the viewpoint of forming a composite structure. There is a need. On the other hand, in order to obtain a good r value, excessive addition is not preferable, so the upper limit of the C content is 0.050%, more preferably 0.030%.

・ Si: 0.01-1.0%
Si promotes ferrite transformation and increases the C content in untransformed austenite to facilitate the formation of a composite structure of ferrite phase and martensite phase, and has an effect of strengthening solid solution. In order to acquire the said effect, it is preferable to contain 0.01% or more of Si, More preferably, 0.05% or more is contained. On the other hand, if Si is contained in excess of 1.0%, a red scale is generated during hot rolling, which deteriorates the surface appearance of the steel sheet. Also, when hot dip galvanizing is performed, the wettability of the plating is deteriorated, resulting in uneven plating and the plating quality is deteriorated. Therefore, the upper limit of the Si content is 1.0%, more preferably 0.7%. .

・ Mn: 1.0-3.0%
Mn is effective in increasing strength and has the effect of slowing down the critical cooling rate at which a martensite phase is obtained, and promotes the formation of the martensite phase during cooling after annealing, so the required strength level and after annealing It is preferable to contain it according to the cooling rate. Mn is also an effective element for preventing hot cracking due to S. From such a viewpoint, it is necessary to contain 1.0% of Mn. More preferably, the content is 1.2% or more. On the other hand, excessive Mn addition exceeding 3.0% degrades the r value and weldability, so the upper limit of the Mn content is 3.0%.

・ P: 0.005-0.1%
P is an element that exhibits the effect of solid solution strengthening. However, if the P content is less than 0.005%, not only the effect does not appear, but also the dephosphorization cost increases in the steelmaking process. Therefore, the P content is 0.005% or more, more preferably 0.01% or more. On the other hand, the addition of excess P exceeding 0.1% causes P to segregate at the grain boundaries and deteriorates secondary work embrittlement resistance and weldability. Moreover, when it is set as the hot dip galvanized steel sheet, the diffusion of Fe from the steel sheet to the plated layer at the interface between the plated layer and the steel sheet is suppressed during the alloying process after the hot dip galvanizing, and the alloying processability is deteriorated. Therefore, an alloying treatment at a high temperature is required, and the obtained plating layer is not preferable because plating peeling such as powdering and chipping is likely to occur. Therefore, the upper limit of the P content is set to 0.1%.

-S: 0.01% or less S is an impurity and causes hot cracking, and also exists as inclusions in steel and deteriorates various properties of the steel sheet. Therefore, it is preferable to reduce as much as possible, but up to 0.01% Since the S content is acceptable, the upper limit of the S content is set to 0.01%.

・ Al: 0.005% to 0.1%
In addition to being useful as a deoxidizing element for steel, Al is an element that exhibits the effect of fixing solute N and improving the normal temperature aging resistance. In order to exhibit such an effect, the Al content needs to be 0.005% or more. On the other hand, the addition of Al exceeding 0.1% causes an increase in alloy cost and further induces surface defects, so the upper limit of Al content is 0.1%.

・ N: 0.01% or less If N is too much, it deteriorates the aging resistance at room temperature and requires a large amount of Al or Ti addition, so it is preferable to reduce it as much as possible, but if the N content is up to 0.01% Since it is acceptable, the upper limit of N content is 0.01%.

・ Nb: 0.03 to 0.3% and 0.2 ≦ (Nb / 93) / (C / 12) ≦ 0.7
Nb is the most important element in the present invention, and has an effect of refining the hot-rolled sheet structure and precipitating and fixing C as NbC in the hot-rolled sheet, and contributes to increasing the r value. In addition, the amount of accumulated strain in the final finish during rolling is improved. From such a viewpoint, Nb is preferably contained in an amount of 0.03% or more. On the other hand, in the present invention, solid solution C for forming a martensite phase is required in the cooling process after annealing, but excessive Nb addition hinders this, so the upper limit of the Nb content is limited to 0.3. %.

  In order to achieve the effect of Nb addition, the ratio of the Nb content (mass%) and the C content (mass%) should be in the range of 0.2 ≦ (Nb / 93) / (C / 12) ≦ 0.7. It is necessary to be satisfied. In addition, Nb and C in a formula here are content (mass%) of each element. When (Nb / 93) / (C / 12) is less than 0.2, the amount of dissolved C is large, and the formation of {111} recrystallized texture effective for increasing the r value is inhibited. Further, if (Nb / 93) / (C / 12) exceeds 0.7, the amount of solute C necessary to form the martensite phase is prevented from being present in the steel, so that the martensite phase is finally obtained. The structure | tissue which has the 2nd phase containing is not obtained. Therefore, the Nb content is in the range of 0.03 to 0.3%, and the ratio of the Nb content to the C content (mass%) is in the range of 0.2 ≦ (Nb / 93) / (C / 12) ≦ 0.7. Satisfied.

The above is the basic component of the present invention.
In the present invention, in addition to the above-described composition, one or two of Mo and Ti shown below may be added.

・ Mo: 0.5% or less
Mo, like Mn, has the effect of slowing the critical cooling rate at which a martensite phase is obtained, and is an element that promotes the formation of a martensite phase during cooling after annealing, and is effective in improving the strength level. Mo is also an element that has the effect of precipitating and fixing C and contributes to an increase in the r value. Mo may be contained in the steel as an inevitable impurity in a range of less than 0.02%. However, in order to obtain the above effect, Mo is preferably contained in an amount of 0.02% or more, and 0.05% or more. More preferably. However, adding excess Mo not only saturates these effects but also increases alloy costs, so the upper limit of the Mo content is preferably 0.5%.

-Ti: 0.1 mass% or less, and the contents of Ti, S, and N in the steel satisfy the relationship of (Ti / 48) / {(S / 32) + (N / 14)} ≤2.
Ti is an element having the effect of precipitating and fixing solute N equivalent to or more than Al. Ti may be contained in the steel as an inevitable impurity in a range of less than 0.005%. To obtain the above effect, the Ti content is preferably 0.005% or more. However, the addition of excessive Ti exceeding 0.1% not only increases the alloy cost, but also prevents the solid solution C necessary for the formation of the martensite phase from remaining in the steel due to the formation of TiC, so the Ti content is 0.1% or less. Further, Ti needs to satisfy (Ti / 48) / {(S / 32) + (N / 14)} ≦ 2 in relation to the S and N contents that are preferentially bonded in the steel. If (Ti / 48) / {(S / 32) + (N / 14)} is greater than 2, the amount of solid solution C during two-phase annealing decreases due to excess Ti, making it difficult to form a composite structure. It is.

  In the present invention, the balance other than the above-described components is preferably substantially composed of iron and inevitable impurities.

  In addition, there is no problem even if B, Ca, REM, and the like are contained within the normal steel composition range. For example, B is an element having an effect of improving the hardenability of steel and can be contained as necessary. However, when the content exceeds 0.003% by mass, the effect is saturated, so the B content is preferably 0.003% by mass or less. Moreover, Ca and REM have the effect | action which controls the form of a sulfide type inclusion, and, thereby, prevents the deterioration of the various characteristics of a steel plate. Since such an effect is saturated when the content of one or two selected from Ca and REM exceeds 0.01% by mass in total, the content is preferably made less than this.

  Other inevitable impurities include, for example, Sb, Sn, Zn, Co, etc. The allowable ranges of these contents are Sb: 0.01% by mass or less, Sn: 0.1% by mass or less, Zn: 0.01 It is the range of the mass% or less and Co: 0.1 mass% or less.

Next, the reason why the steel structure and mechanical properties of the steel sheet of the present invention are limited will be described below.
The high-strength steel sheet according to the present invention has a steel structure including a ferrite phase having an area ratio of 50% or more and a martensite phase having an area ratio of 1% or more after satisfying the above steel composition, and an average r value. It must be 1.2 or more, and the product of tensile strength (TS) and elongation (El) (TS x El) must be 19000 MPa ·% or more.

-It has a steel structure containing a ferrite phase with an area ratio of 50% or more and a martensite phase with an area ratio of 1% or more. The high-strength steel sheet of the present invention has a ferrite phase with an area ratio of 50% or more and an area ratio. And a steel sheet having a composite structure containing a martensite phase of 1% or more. Here, the steel sheet of the present invention has developed a {111} recrystallized texture of the ferrite phase occupying more than half of the area ratio, and has achieved an average r value ≧ 1.2. In order to obtain a steel sheet with good deep drawability and tensile strength TS ≧ 440MPa, it is necessary to have a steel structure containing a ferrite phase with an area ratio of 50% or more and a martensite phase with an area ratio of 1% or more. There is. When the ferrite phase is reduced and the area ratio is less than 50%, it becomes difficult to ensure good deep drawability, and the press formability tends to decrease. More preferably, the ferrite phase is 70% or more in area ratio. In order to take advantage of the composite structure, the ferrite phase is preferably 99% or less. Here, the ferrite phase means a polygonal ferrite phase or a bainitic ferrite phase having a high dislocation density transformed from an austenite phase.

  In the present invention, the martensite phase must be present, and the martensite phase needs to be contained in an area ratio of 1% or more. If the martensite phase is less than 1%, it is difficult to obtain a good strength-ductility balance. The martensite phase is more preferably 3% or more.

  The steel structure of the steel sheet of the present invention may be a structure containing pearlite, bainite, retained austenite (γ) phase, etc. in addition to the above-described ferrite phase and martensite phase.

-The average r value is 1.2 or more The steel sheet of the present invention is required to satisfy the above-described component composition and steel structure, and to satisfy the average r value ≧ 1.2. In the present invention, the steel composition containing the ferrite phase and the martensite phase is adjusted to the above component composition, and for the first time, an average r value of 1.2 or more can be achieved. Here, the average r value means an average plastic strain ratio determined by JIS Z 2254, and is a value determined below.
Average r value = (r ₀ + 2r ₄₅ + r ₉₀ ) / 4
However, r ₀ , r ₄₅ and r ₉₀ are plastic strain ratios obtained by measuring the test pieces taken in parallel, 45 ° direction and 90 ° direction, respectively, with respect to the rolling direction of the plate surface.

・ The product TS × El of tensile strength TS and elongation El is 19000 MPa ·% or more. The steel sheet of the present invention is characterized by an excellent balance between strength and ductility, and the value of TS × El is 19000 MPa ·% or more. It is necessary to be. In this case, El is a tensile test using a JIS No. 5 test piece in accordance with the provisions of JIS Z 2241, and is defined as the total elongation at break.

  The steel sheet of the present invention also includes a so-called plated steel sheet having a plating layer on the surface thereof subjected to surface treatment such as electroplating or hot dip galvanizing. The term “plating” as used herein refers to conventional steel sheets such as zinc-based alloy plating in which zinc is the main component and alloy elements are added in addition to pure zinc, or Al-based alloy plating in which alloy elements are mainly composed of Al or Al. Also includes a plating layer applied to the surface.

Next, the preferable manufacturing method of this invention steel plate is demonstrated.
Since the composition of the slab used in the production method of the present invention is the same as that of the steel plate described above, the reason for limiting the steel slab is omitted.

  The steel sheet of the present invention comprises a steel slab having a composition within the above-described range as a material, a hot rolling step in which the material is hot-rolled to form a hot-rolled sheet, and pickling and cold-rolling the hot-rolled sheet. Can be produced by sequentially performing a cold rolling step to form a cold-rolled sheet and a cold-rolled sheet refrigeration step for achieving recrystallization and complex structure formation on the cold-rolled sheet.

  In the present invention, first, when the steel slab is made into a finish rolling exit temperature FT (° C.) by hot rolling and the total rolling reduction of the final three stands of finish rolling is X (%), the finish rolling exit temperature FT is 800 ≦ FT ≦ 800 + 25 × X × Nb (Nb in the formula is Nb content in steel (mass%)), and after finish rolling, cool at 25 ° C / s or more within 0.5 seconds And the hot rolling process which makes a coiled hot rolled sheet at a coiling temperature: 500-720 degreeC is given.

  The steel slab used in the production method of the present invention is preferably produced by a continuous casting method in order to prevent macro segregation of components, but may be produced by an ingot-making method or a thin slab casting method. In addition to the conventional method in which the steel slab is manufactured and then cooled to room temperature and then heated again, direct feed rolling in which the steel slab is charged without being cooled and charged in a heating furnace and hot-rolled, or a little heat retention Energy saving processes such as direct feed rolling and direct rolling, which are hot-rolled immediately after performing the above, can be applied without any problem.

  The slab heating temperature is preferably low because the precipitates are coarsened to develop a {111} recrystallized texture and improve deep drawability. However, if the heating temperature is less than 1000 ° C, the rolling load increases and the risk of trouble occurring during hot rolling increases, so the slab heating temperature is preferably 1000 ° C or higher. Note that the upper limit of the slab heating temperature is preferably set to 1300 ° C. because of an increase in scale loss accompanying an increase in oxidized weight.

  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 determined according to a conventional method. It goes without saying that using a so-called sheet bar heater for heating the sheet bar is an effective method from the viewpoint of lowering the slab heating temperature and preventing troubles during hot rolling.

  Next, the sheet bar is finish-rolled to obtain a hot-rolled sheet. When the finish rolling exit temperature FT is 800 ° C. or higher, the finish rolling exit temperature is FT (° C.), and the total rolling reduction of the final three stands of finish rolling is X (%), 800 ≦ FT ≦ 800 + 25 Finish rolling is performed with × X × Nb (Nb in the formula is Nb content (% by mass) in steel). In the present invention, it is important to sufficiently accumulate strain at the final stage of finish rolling, to promote ferrite transformation, and to refine and homogenize. Further, as described above, Nb affects the amount of accumulated strain and contributes to improvement of the amount of accumulated strain by delaying recrystallization between the rolling stands. Based on these results, various experiments were conducted to analyze the effects of the total reduction ratio X and Nb content of the final three stands of FT and finish rolling on the r value and TS × El, and r ≧ 1.2 and TS × El ≧ 19000 MPa. -FT ≦ 800 + 25 × X × Nb was determined as an empirical formula for obtaining%. If the value of FT exceeds the value obtained from the formula given by 800 + 25 × X × Nb, the structure becomes coarse and the formation and development of {111} recrystallized texture after cold rolling annealing is prevented, resulting in a high r value. Is not preferable, and the strength-ductility balance is deteriorated. The meaning of this equation is not necessarily clear, but Nb has an effect of accumulating rolling strain. Therefore, if the amount of Nb is large, the same effect can be exhibited even at a higher finishing temperature.

  However, when the FT is less than 800 ° C., the structure becomes a processed structure, and not only the {111} texture develops after cold rolling annealing, but also the rolling load during hot rolling increases. Therefore, FT is 800 ° C. or higher, and FT is 800 + 25 × X × Nb or lower.

  Moreover, in order to reduce the rolling load at the time of hot rolling, it is good also as lubrication rolling between some or all passes of finishing rolling. Lubrication rolling is also effective from the viewpoint of homogenizing the shape of the steel sheet and homogenizing the material. The coefficient of friction during lubrication rolling is preferably in the range of 0.10 to 0.25. Furthermore, it is also preferable to use a continuous rolling process in which the adjacent sheet bars are joined and finish-rolled continuously. It is desirable to apply the continuous rolling process from the viewpoint of the operational stability of hot rolling.

  After the finish rolling, cool at 25 ° C./s or more within 0.5 seconds. This is because it is necessary to freeze the structure in the finish rolling in order to effectively transform the strain accumulated due to the effect of Nb into ferrite, and for this purpose, cooling is performed within 0.5 seconds after the finish rolling. The cooling rate must be 25 ° C / s or higher. The cooling stop temperature depends on the length of the runout table, but the winding temperature may be set as follows.

  The coil winding temperature CT is in the range of 500 to 720 ° C. This temperature range is a suitable temperature range for precipitating NbC in the hot-rolled sheet and making the hot-rolled structure uniform and fine, and especially when CT exceeds the upper limit, the crystal grains become coarse and cause a decrease in strength. This will hinder high r-value after cold rolling annealing. The coil winding temperature CT is preferably 550 to 680 ° C.

  By adjusting the component composition and hot rolling conditions as described above, 1) 20% or more of the total C content can be deposited and fixed as NbC at the hot rolling stage, and 2) In addition, the average crystal grain size including a low-angle grain boundary can be 8 μm or less, which is advantageous for increasing the r value.

1) The amount of C deposited and fixed as NbC in the hot-rolled sheet stage is 20% or more of the total amount of C
The amount of C deposited and fixed as NbC is a value calculated by the following equation from the amount of precipitated Nb obtained by chemical analysis (extraction analysis) of a hot-rolled sheet.
C _fix (%) = {12 × (Nb _Pre / 93) / C _total } × 100
However, C _fix is the ratio (%) of the C amount precipitated and fixed as NbC to the total C amount, C _total is the total C amount (mass%) in the steel, and Nb _Pre is the precipitated Nb amount (mass%). ).

  Reducing solute C at the stage before cold rolling and recrystallization is effective for increasing the r value, and in the present invention, the amount of C precipitated and fixed as NbC is 20% or more of the total amount of C. The effect appears. On the other hand, the upper limit of the Nb content is no problem as long as the upper limit (Nb / 93) / (C / 12) ≦ 0.7 of the other appropriate range described above is satisfied. And the formation of both.

2) The average grain size of the hot-rolled sheet is 8 μm or less, including an average grain size including a low-angle grain boundary. In conventional mild steel sheets, it is known that the finer the grain size of the hot-rolled sheet, the higher the r value. It has been. In the present invention, particularly when the particle diameter is measured including a low-angle grain boundary, an effect appears in increasing the r value when the average crystal grain diameter is 8 μm or less. The method of measuring the crystal grain size, the cross section parallel to the rolling direction (L cross section) imaging the microstructure have an optical microscope, by a cutting method in accordance with JIS G O552, is determined as the nominal diameter d _n Alternatively, it may be obtained using a device such as EBSD (Electron Back-Scatter Diffraction).

  Next, the hot-rolled sheet is pickled and cold-rolled to give a cold-rolling step to obtain a cold-rolled sheet. Pickling may be performed under normal conditions. The cold rolling condition is not particularly limited as long as it can be a cold-rolled sheet having a desired size and shape, but the rolling reduction during cold rolling is preferably at least 40%, more preferably 50% or more. And A high cold rolling reduction is generally effective for increasing the r value. If the reduction is less than 40%, the {111} recrystallization texture does not develop, and it may be difficult to obtain excellent deep drawability. is there. On the other hand, in this invention, the r value increases as the cold rolling reduction is increased in the range up to 90%, but when it exceeds 90%, not only the effect is saturated, but also the load on the roll during rolling increases. The upper limit of the rolling reduction is preferably 90%.

  Next, the cold-rolled sheet pure process is performed by annealing the cold-rolled sheet at an annealing temperature of 800 to 950 ° C., and then cooling at an average cooling rate in the temperature range from the annealing temperature to 500 ° C. at 5 ° C./s or more. Apply.

  The annealing is preferably performed in a continuous annealing line in order to ensure the cooling rate required in the present invention, and it is necessary to perform in a temperature range of 800 to 950 ° C. In the present invention, by setting the annealing temperature, which is the highest temperature during annealing, to approximately 800 ° C. or higher, a two-phase region of α-γ, that is, a structure containing a ferrite phase and a martensite phase after cooling can be obtained. It can be higher than the temperature and higher than the recrystallization temperature. That is, when the annealing temperature is less than 800 ° C., a sufficient martensite phase is not formed after cooling, or recrystallization is not completed and the ferrite texture cannot be adjusted, so that a high r value cannot be achieved. On the other hand, at a high temperature exceeding 950 ° C., the recrystallized grains are remarkably coarsened and the characteristics are remarkably deteriorated.

  The cooling rate after the annealing needs to be cooled by setting the average cooling rate in the temperature range from the annealing temperature to 500 ° C. to 5 ° C./s or more from the viewpoint of forming the martensite phase. When the average cooling rate in the temperature range is less than 5 ° C./s, the martensite phase is hardly formed, and a ferrite single phase structure is formed, resulting in insufficient structure strengthening.

  In the present invention, since the presence of the second phase including the martensite phase is essential, the average cooling rate up to 500 ° C. is required to be equal to or higher than the critical cooling rate. Satisfactory when the temperature is set to ℃ / s or more. In addition, although it does not specifically limit about cooling below 500 degreeC, It is preferable to continue cooling at an average cooling rate of 5 degree-C / s or more desirably to 300 degreeC, and when overaging treatment is performed, overaging treatment is preferable. It is preferable that the average cooling rate is 5 ° C./s or higher up to the temperature.

  Moreover, after the cold-rolled sheet annealing step, a plating process such as an electroplating process or a hot dipping process may be performed to form a plating layer on the steel sheet surface.

  For example, when performing a hot dip galvanizing process often used for automotive steel sheets as a plating process, the annealing is performed in a continuous hot dip plating line, and immersed in a hot dip galvanizing bath following cooling after annealing, A hot-dip galvanized layer may be formed on the surface, or an alloying treatment may be further performed to produce an alloyed hot-dip galvanized steel sheet. In this case, it is preferable that the cooling after leaving the hot-dip plating pot or after alloying is performed so that the average cooling rate up to 300 ° C. is 5 ° C./s or more.

  Further, the cooling after the annealing may be performed in an annealing line, and after cooling to room temperature, hot dip galvanizing may be performed in a hot dip galvanizing line, or further alloying treatment may be performed. Here, the plating layer is not limited to pure zinc and zinc-based alloy plating, and may of course be various plating layers conventionally applied to the steel sheet surface, such as Al or Al-based alloy plating.

  Further, the cold-rolled annealed plate and the plated steel plate may be subjected to temper rolling or leveler processing for the purpose of adjusting shape correction, surface roughness, and the like. The total elongation of temper rolling or leveler processing is preferably in the range of 0.2 to 15%. If the elongation is less than 0.2%, shape correction and roughness adjustment cannot be performed sufficiently, and the intended purpose cannot be achieved. On the other hand, when the elongation rate exceeds 15%, the ductility is significantly reduced. In addition, although the processing form differs between temper rolling and leveler processing, it has been confirmed that there is no significant difference between the two.

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 to 1250 ° C. and roughly rolled into sheet bars, and then hot-rolled sheets were formed by a hot rolling process in which finish rolling under the conditions shown in Tables 2 and 3 was performed. These hot-rolled sheets were made into cold-rolled sheets by pickling and a cold rolling process with a rolling reduction of 65%. Subsequently, these cold-rolled sheets were subjected to continuous annealing in the continuous annealing line under the conditions shown in Tables 2 and 3. Further, the obtained cold-rolled annealed sheet was subjected to temper rolling with an elongation of 0.5%. In addition, the No. 2 steel plate is subjected to a cold plate annealing process in a continuous hot dip galvanizing line, followed by in-line hot dip galvanizing (plating bath temperature: 480 ° C) to obtain a hot dip galvanized steel plate. Various characteristics were evaluated.

  About the obtained cold-rolled annealed sheet, steel structure, tensile properties (yield stress YS, tensile strength TS, elongation El, and product of tensile strength (TS) and elongation (El) (TS x El)) and r value investigated. The survey method is as follows.

(1) Steel structure of cold-rolled annealed plates Test specimens were collected from each of the obtained cold-rolled annealed plates or plated steel plates, and the cross section (L cross section) parallel to the rolling direction was finely measured using an optical microscope or scanning electron microscope. The visual tissue was imaged, and the area ratio of the ferrite phase, which is the main phase, and the type and area ratio of the second phase were obtained by an image analysis apparatus.

(2) Tensile properties of cold-rolled annealed plates JIS No. 5 tensile test specimens were taken from each of the obtained cold-rolled annealed plates or plated steel plates in the 90 ° direction (C direction) with respect to the rolling direction. In accordance with the tensile test at a crosshead speed of 10 mm / min, yield stress (YS), tensile strength (TS), elongation (El), and the product of tensile strength (TS) and elongation (El) (TS x El )

(3) Measurement of r value of cold-rolled annealed sheet From each of the obtained cold-rolled annealed sheets or plated steel sheets, the rolling direction (L direction), 45 ° direction (D direction) with respect to the rolling direction, and 90 direction with respect to the rolling direction, respectively. A JIS No. 5 tensile test piece was taken in the direction (C direction). Obtain the width strain and thickness strain of each specimen when 10% uniaxial tensile strain is applied to these specimens, and obtain the average r value (average plastic strain ratio) in accordance with the provisions of JIS Z 2254. This is the r value.

  As is clear from Tables 2 and 3, all of the inventive examples have a tensile strength TS of 440 MPa or higher, an average r value of 1.2 or higher, and a high strength-ductility balance. ing. On the other hand, the comparative example manufactured on the conditions which remove | deviate from the range of this invention is a steel plate which intensity | strength is insufficient or r value or intensity-ductility balance is falling.

  According to the present invention, a high-strength steel sheet having a tensile strength TS of 440 MPa or more, an average r value of 1.2 or more, TS × El of 19000 MPa ·% or more and a high r value, and an excellent balance between strength and ductility is inexpensive. And it becomes possible to manufacture stably, and there exists a remarkable effect on an industry. For example, when the high-strength steel sheet of the present invention is applied to automobile parts, it is possible to increase the strength of parts that have been difficult to press-form so far, and it is possible to sufficiently contribute to collision safety and weight reduction of the automobile body. . Moreover, it is applicable not only to automobile parts but also to household appliance parts and pipe materials.

Claims (8)

% By mass
C: 0.010 to 0.050%
Si: 0.01 to 1.0%
Mn: 1.0-3.0%
P: 0.005-0.1%
S: 0.01% or less,
Al: 0.005-0.1%
N: 0.01% or less and
Nb: 0.03-0.3%
And Nb content and C content are 0.2 ≦ (Nb / 93) / (C / 12) ≦ 0.7 (Nb and C in the formula are the contents (mass%) of each element) The relationship is satisfied, and the balance has a steel composition containing a component composition consisting essentially of Fe and inevitable impurities, and including a ferrite phase with an area ratio of 50% or more and a martensite phase with an area ratio of 1% or more. The average r value is 1.2 or more, and the product of tensile strength (TS) and elongation (El) (TS × El) is 19000 MPa ·% or more. Excellent high strength steel plate.   In addition to the said composition, Mo: 0.5% or less is further contained in the mass%, The high strength steel plate excellent in the deep drawability and strength-ductility balance of Claim 1 characterized by the above-mentioned.   In addition to the above composition, Ti: 0.1% or less by mass%, and the contents of Ti, S and N in the steel are (Ti / 48) / {(S / 32) + (N / 14)} ≦ 2 (wherein Ti, S and N are the contents (mass%) of each element) The deep drawability and strength according to claim 1 or 2, High strength steel plate with excellent ductility balance.   The high strength steel sheet excellent in deep drawability and strength-ductility balance according to any one of claims 1 to 3, wherein the surface has a plating layer. % By mass
C: 0.010 to 0.050%
Si: 0.01 to 1.0%
Mn: 1.0-3.0%
P: 0.005-0.1%
S: 0.01% or less,
Al: 0.005-0.1%
N: 0.01% or less and
Nb: 0.03-0.3%
And Nb and C content (mass%) is 0.2 ≦ (Nb / 93) / (C / 12) ≦ 0.7 (where Nb and C are the contents of each element (mass%) )) When the steel slab having a composition satisfying the above) is hot-rolled and the finish rolling exit temperature is FT (° C.) and the final rolling reduction of the final three stands is X (%), the finish rolling exit The temperature FT is 800 ≦ FT ≦ 800 + 25 × X × Nb (where Nb is the Nb content (mass%) in the steel) and is subjected to finish rolling, and 25 ° C./s within 0.5 seconds after the finish rolling A cold rolling process in which the steel sheet is cooled and rolled at a coiling temperature of 500 to 720 ° C. to be a hot rolled sheet, and the hot rolled sheet is pickled and cold rolled to form a cold rolled sheet. The cold rolled sheet is annealed at an annealing temperature of 800 to 950 ° C., and then cooled at an average cooling rate of 5 ° C./s or more in the temperature range from the annealing temperature to 500 ° C. Characterized by sequential application To deep drawability and strength - the method of producing a high strength steel sheet excellent in ductility balance.   6. The method for producing a high strength steel plate excellent in deep drawability and strength-ductility balance according to claim 5, wherein the steel slab further contains Mo: 0.5% or less by mass% in addition to the above composition.   In addition to the above composition, the steel slab further contains Ti: 0.1% or less by mass%, and the content of Ti, S and N in the steel is (Ti / 48) / {(S / 32) + (N / 14)} ≦ 2 (wherein Ti, S and N are the contents (mass%) of each element) The deep drawability and the strength-ductility balance according to claim 5 or 6 are satisfied. For producing high-strength steel sheets with excellent resistance.   A high-strength steel sheet excellent in deep drawability and strength-ductility balance, characterized in that in the manufacturing method according to any one of claims 5 to 7, a plating treatment is performed after the cold-rolled sheet annealing step. Manufacturing method.