JP4679195B2 - Low yield ratio high tension hot dip galvanized steel sheet manufacturing method - Google Patents

Description

  The present invention relates to a method for producing a low yield ratio high-tensile hot-dip galvanized steel sheet for automobile steel sheets, building structural members, and home appliances that has an excellent balance between strength and ductility and exhibits a low yield ratio.

In recent years, weight reduction of automobiles has been studied for the purpose of improving fuel efficiency from the viewpoint of global environmental protection, and weight reduction of parts used has been attempted. Steel sheets used for these applications have been increased in tension from the viewpoint of ensuring a desired strength even when thinned.
By the way, since many of the steel plates for motor vehicles are shape | molded by press work, the outstanding press-formability is calculated | required by these steel plates. The material properties that serve as an indicator of excellent press formability include a high r value and a low surface friction resistance, but high ductility is required. At the same time, in order to stabilize the press formability, it is important to lower the yield stress of the steel sheet compared to the tensile strength, that is, to lower the yield ratio. On the other hand, in automobile parts, corrosion resistance is often required depending on the part used. In this case, an alloyed galvanized steel sheet having excellent electrodeposition coating properties is often used in hot dip coating.
Thus, in order to reduce the weight of automobile parts, a high-tensile alloyed galvanized steel sheet excellent in ductility is required. At the same time, it is also important that it can be manufactured inexpensively and industrially stably.

From these technical problems, a technique using retained austenite has been proposed as a conventional technique focusing on a high-tensile steel sheet exhibiting high ductility as a plating material.
In Patent Document 1, a steel sheet containing C: 0.30 to 0.55%, Si: 0.7 to 2.0%, Mn: 0.5 to 2.5% is heated to an austenite single phase region, By holding at 650 to 750 ° C. for 4 to 15 seconds, and subsequently holding at 450 to 650 ° C. in the subsequent cooling process for a total of 10 to 50 seconds, “10% or more by volume in martensite or bainite” It has been proposed to obtain a “high-strength steel sheet exhibiting high ductility” by causing a “composite structure including ferrite and retained austenite” to appear.

In Patent Document 2, C: 0.12 to 0.55%, Si: 0.4 to 1.8%, Mn: 0.2 to 2.5%, and an appropriate amount of P, Ni, if necessary A steel sheet containing one or more of Cu, Cr, Ti, Nb, V, and Mo is heated to a “ferrite + austenite single phase region” and then held at a temperature range of 500 to 350 ° C. during the cooling for 30 seconds to 30 minutes. Thus, it has been proposed that a “high strength steel sheet exhibiting high ductility” is obtained by causing “ferrite + bainite + residual austenite composite structure” to appear.
Further, Patent Document 3 proposes a Si-added type retained austenite-containing steel sheet that uses Si as an element for suppressing carbide formation and stabilizing retained austenite. Patent Document 3 also shows that the impact resistance is further improved by adding Ti and Nb to form carbonitrides thereof.
JP 60-43464 A JP-A 61-157625 JP-A-6-145808

  However, the techniques proposed in Patent Documents 1 and 2 have obtained high ductility by using transformation-induced plasticity (TRIP) due to retained austenite, and temperature conditions in annealing and plating processes to obtain retained austenite. However, unlike a general alloyed galvanized steel sheet, a special heat cycle is required, resulting in an increase in manufacturing cost. Specifically, it is necessary to cause bainite transformation to proceed in the cooling step after annealing and to concentrate C in the remaining austenite. Moreover, although the ductility of the steel plate containing these retained austenites is certainly high, it may become excessive ductility depending on the use.

Moreover, since Si and Mn which are more easily oxidized than Fe are contained for increasing the strength, Si and Mn oxides are easily generated on the steel sheet surface during annealing. These oxides cause adverse effects such as significantly reducing plating adhesion and alloy speed. Therefore, a proposal for controlling the annealing atmosphere has been proposed for these improvements, but the effect is limited, and it is insufficient to ensure stable adhesion of plating.
On the other hand, as in Patent Document 3, in the case of increasing the strength using a carbonitride precipitate based on the addition of Ti or Nb, the yield ratio increases. For this reason, there is also a problem that the shape freezing property is inferior when press forming generally adopted as a forming method of an automobile steel plate is adopted.
The present invention has been devised to solve such problems, and provides a high-tensile hot-dip galvanized steel sheet that stably exhibits a good strength-ductility balance and has a low yield ratio and excellent plating adhesion. It aims at obtaining by a normal continuous annealing-hot-dipping process.

  In order to achieve the object, the low yield ratio high-tensile hot-dip galvanized steel sheet according to the present invention has a C: 0.03 to 0.18 mass%, Si: 0.1 to 0.5 mass%, and Mn: 1.0 to 2.5 mass%, P: 0.03 mass% or less, S: 0.005 mass% or less, and if necessary, Cr: 0.1-0.5 mass% and Mo: 0 After forming an Fe-based plating layer on a steel sheet having a composition comprising the remaining Fe and unavoidable impurities including one or two of 0.03 to 0.3% by mass, annealing is performed in a ferrite + austenite two-phase region. After the volume fraction of the ferrite phase is adjusted to 20 to 50%, it is cooled to 650 to 500 ° C. at an average cooling rate of 5 to 20 ° C./second as primary cooling, and then continuously to the galvanizing bath temperature as secondary cooling. Cooling at 5 ° C./second or less, the volume fraction of ferrite phase after cooling is 50 to 70% And, wherein the performing molten zinc plating and alloying treatment after this.

The adhesion amount of the Fe-based plating layer is preferably 1 to 6 g / m ² and the annealing temperature is preferably 700 to 900 ° C.
When the steel sheet treated under the above conditions is subjected to hot dip galvanization and alloying treatment and cooled to room temperature, the metal structure is in volume ratio, the ferrite phase is 60 to 80%, the low temperature transformation phase is 10 to 30%, It has a composite structure with a pearlite phase of 10% or less.

  In the present invention, carbon nitride-forming elements such as Ti and Nb are not used, and the structure after mainly adding C, Si, and Mn, and the structure after hot dip galvanizing and alloying treatment are combined with a ferrite + low temperature transformation phase. By using a phase structure, a low yield ratio and a high ductility can be achieved. In addition, the above-described multi-phase structure can be stably achieved by strict control of temperature-cooling conditions at each stage in a normal continuous annealing-hot-dipping line, so that the balance between strength and ductility is excellent, and a low yield ratio is achieved. The high-tensile hot-dip galvanized steel sheet exhibiting the above can be manufactured at low cost and industrially stably.

The inventors have used steel sheets containing Si and Mn as raw materials without adding carbonitride-forming elements such as Ti and Nb as raw materials, and are excellent in press formability and yet have the required strength. Various studies have been made on techniques for producing a high-tensile hot-dip galvanized steel sheet having a good balance of ductility in a normal continuous annealing-hot dip plating line.
As a result, the processing temperature and cooling rate in each process are strictly regulated and an appropriate structure is created in each process, so that the structure after hot dip galvanizing and alloying treatment can be obtained even in a normal continuous annealing-hot-plating line. A multiphase structure of ferrite + low-temperature transformation phase could be obtained, and a high-tensile hot-dip galvanized steel sheet that achieved both low yield ratio and high ductility could be obtained.

In the present invention, in order to reduce the yield ratio, carbonitride-forming elements such as Ti and Nb are not used, and basically high strength is achieved with C, Si, and Mn. Moreover, Ar ₃ transformation point is lowered by Mn, and pearlite transformation during cooling after annealing is suppressed. Furthermore, the ferrite transformation is further advanced through primary cooling and secondary cooling after annealing, and a two-phase structure of mainly ferrite and austenite is formed until the plating layer is alloyed. From the above, by generating a low temperature transformation phase of martensite + bainite, a high strength steel plate having a multiphase structure composed of ferrite and a low temperature transformation phase and having an excellent strength-ductility balance can be finally obtained.
The details will be described below.

In producing the low yield ratio high tension hot dip galvanized steel sheet of the present invention, first, the component composition of the steel is determined as follows.
C: 0.03 to 0.18% by mass
C is an element effective for increasing the strength of steel, and is concentrated in austenite during annealing in the two-phase region, and contributes to the generation of a low temperature transformation phase effective for increasing the strength during subsequent cooling. These effects cannot be obtained unless the content is less than 0.03 mass%. On the other hand, if the content exceeds 0.18% by mass, not only does ductility decrease due to excessive increase in strength, but also weldability deteriorates.

Si: 0.1-0.5% by mass
Si is effective for increasing the strength as a solid solution strengthening element. The effect is not exhibited unless it is less than 0.1% by mass. On the other hand, when the content exceeds 0.5% by mass, the temperature necessary for alloying increases by diffusing from the surface layer of the base metal to the Fe plating layer during annealing to form an oxide. And austenite transforms to pearlite more, the amount of bainite and martensite after plating decreases, and the required strength cannot be obtained.

Mn: 0.5 to 2.5% by mass
Mn is effective for increasing the strength as a solid solution strengthening element. Moreover, by suppressing the pearlite transformation during the primary cooling after annealing, the formation of bainite and martensite is promoted, which contributes to an increase in strength. Further, it has an action of lowering the Ar ₃ transformation point and suppressing pearlite transformation that causes a decrease in strength in primary and secondary cooling. These effects are not exhibited unless the content is less than 0.5% by mass. On the other hand, if the content exceeds 2.5% by mass, the strength is excessively increased, ductility is lowered and workability is deteriorated, and the plating adhesion is lowered similarly to Si.

P: 0.03 mass% or less P contributes to high strength as a stable solid solution strengthening element. However, when it is contained in a large amount, grain boundary segregation becomes prominent, and the toughness of the steel sheet is remarkably deteriorated. Therefore, the upper limit of P is 0.03 mass%.
S: 0.005 mass% or less S is preferably present in the steel sheet mainly as MnS, and is preferably less because it deteriorates the ductility of the steel sheet. In the present invention, the upper limit of the S content is 0.005% by mass.

Moreover, in this invention, you may add 1 type or 2 types of Cr and Mo which have the effect | action which suppresses the pearlite transformation which causes a strength fall by primary and secondary cooling as needed. In the case of Cr, 0.1% by mass is contained, and in the case of Mo, 0.03% by mass is effective. However, if any of them is contained in a large amount, the toughness is lowered. Therefore, when Cr is added, the upper limit is 0.5% by mass for Cr and 0.3% by mass for Mo.
Except for Al added as a deoxidizer, the components other than those described above are impurities.

Next, the role and means of each manufacturing process will be described in detail.
After making it into a slab by continuous casting, hot rolling is performed while it is hot, or after being cooled to room temperature, hot rolling is performed to obtain a hot-rolled steel sheet. The hot rolling may be performed under normal conditions without any limitation on the soaking temperature, the rolling temperature, etc. From the viewpoint of the load during cold rolling and the pickling property, the rolling after hot rolling is 500 A temperature of ˜650 ° C. is preferable.
The wound hot rolled coil is then pickled as usual and then subjected to cold rolling. Although it is not necessary to specifically limit the cold rolling conditions, the cold rolling rate is preferably set to 30% or more in consideration of the sheet passability during the cold rolling.

The cold-rolled sheet is first subjected to Fe-based pre-plating, and then annealed.
It is effective to perform annealing heating after applying Fe-based plating in order to stably prevent deterioration of plating adhesion and alloying speed due to diffusion of Si and Mn added with Fe-based plating before annealing. . If Fe-based plating is not applied, the alloying temperature must be increased, and if an attempt is made to promote alloying, austenite transforms into pearlite, and the amount of low-temperature transformation phase generated in the cooling process after alloying decreases. Therefore, the required strength does not appear.
It is preferable to form the Fe-based plating in the range of 1 to 6 g / m ² of adhesion amount. If the plating adhesion amount is less than 1 g / m ² , the above-mentioned effects are not exhibited. Even if the Fe-based plating layer is thickened, the above action is saturated, resulting in an increase in manufacturing cost. Therefore, the upper limit of the Fe-based plating adhesion amount is 6 g / m ² .
The Fe plating method is not limited, but it is preferable to use an electroplating method.

Annealing In this process, the purpose is to recrystallize the cold-rolled sheet, but annealing is performed in a two-phase region of ferrite and austenite in order to achieve multiphase organization. During this annealing, austenite is formed with the carbide of the cold-rolled sheet as a nucleus. By forming austenite having a high C concentration and forming a low-temperature transformation phase during subsequent cooling, a multiphase structure having both strength and ductility can be obtained. At this time, the volume fraction of austenite has a great influence on the tensile properties of the plated steel sheet through the kind and amount of the low temperature transformation phase generated in the subsequent cooling-plating process. Therefore, it is important to adjust not only the annealing conditions but also the austenite volume ratio to be generated.

  In the present invention, annealing is performed in the range of 700 to 900 ° C. to obtain a two-phase structure having an austenite phase of 50 to 80%, that is, a ferrite phase volume ratio of 20 to 50%. In order to obtain a steel sheet with a good balance between strength and ductility after plating, it is necessary to have a multiphase structure of soft ferrite and a hard low-temperature transformation phase. For this purpose, various transformation phases are generated during cooling after annealing. It is necessary to keep the volume ratio of austenite within a predetermined range. After annealing, if the austenite phase is not in the range of 50 to 80% by volume, then a low-temperature transformation phase having a volume ratio that expresses the desired strength cannot be obtained.

  If the annealing temperature is less than 700 ° C., a large amount of undissolved carbon remains, the austenite amount is low, and the C concentration in the austenite is also low, so the volume ratio of the low-temperature transformation phase generated in the cooling process after annealing. Decreases and the desired strength cannot be obtained. Conversely, if annealing is performed at a high temperature exceeding 900 ° C., the austenite volume fraction becomes excessively large and the C concentration also decreases, so that pearlite is excessively generated in the cooling process after annealing, and the volume of the low-temperature transformation phase. The rate decreases and the desired strength cannot be obtained.

Primary cooling Here, in the continuous annealing-plating step, a period until the steel sheet is immersed in the plating desire is referred to as a cooling zone, the front part is referred to as primary cooling, and the rear part is referred to as secondary cooling.
In the primary cooling process, the ferrite transformation proceeds to decrease the volume fraction of austenite and increase the C concentration. By regulating the cooling rate and the cooling stop temperature, the formation of pearlite, which is an impediment to securing strength and ductility, is suppressed, and austenite that forms a low-temperature transformation phase is left during subsequent cooling.

The cooling stop temperature in the primary cooling process is a requirement that affects the progress of grain growth of recrystallized ferrite during annealing in the two-phase region. If the temperature exceeds 650 ° C., the ferrite volume fraction decreases due to a decrease in the ferrite nucleation rate. On the other hand, if the temperature is lower than 500 ° C., the diffusion rate of Fe is lowered, and the ferrite transformation rate is lowered. In addition, bainite is easily generated by secondary cooling, and C concentration in austenite is prevented.
The cooling rate in the primary cooling process similarly dominates the progress of the ferrite transformation. If it is faster than 20 ° C./second, the progress of ferrite transformation becomes insufficient and austenite having a low C concentration remains, so that the strength of the low temperature transformation phase that is hard and contributes to strength is lowered. Further, since the volume fraction of soft ferrite is lowered, ductility is also lowered. On the other hand, if it is too slow at less than 5 ° C./second, it takes a long time to cool down to the primary cooling stop temperature, leading to an increase in manufacturing cost.

In the secondary cooling process of cooling to the secondary cooling plating bath temperature, it is necessary to advance the ferrite transformation and suppress the pearlite transformation. In order to realize this, it is necessary to regulate the cooling rate below a certain level after lowering the Ar ₃ transformation point by adding Mn as a steel component as described above. Furthermore, it is important to regulate the volume ratio of the low temperature transformation phase generated during cooling after alloying by regulating the structure, particularly the austenite volume ratio, when cooled to a temperature immersed in the plating bath.

If the cooling rate in the secondary cooling process is so fast as to exceed 5 ° C./second, the progress of the ferrite transformation becomes insufficient.
When immersed in the plating bath, it is necessary to adjust the volume ratio of ferrite to 50 to 70% and the volume ratio of austenite to 30 to 50%. In order to generate a hard low temperature transformation phase in the cooling process after plating, austenite having a volume fraction of at least 30% is required. If the volume fraction of ferrite is less than 50%, sufficient ductility cannot be ensured.

Hot-dip galvanization and alloying treatment The steel sheet annealed and cooled to have a predetermined proportion of the two-phase structure is then hot-dip galvanized under normal conditions and alloyed under normal conditions. The cooling rate after alloying is not particularly limited, and normal cooling conditions are employed.
Due to the presence of the Fe-based pre-plated layer, the alloying speed is as fast as usual even if the amount of Si or Mn added is large, so there is no need to change the usual alloying conditions and cooling conditions.

The austenite remaining after the final structure alloying is changed to a low temperature transformation phase without pearlite transformation at a normal cooling rate.
The final metal structure is a composite structure in which the ferrite phase is 60 to 80%, the low temperature transformation phase composed of martensite and bainite is 10 to 30%, and the pearlite phase is 10% or less. If the ferrite phase is less than 60%, the yield ratio increases, and if it exceeds 80%, the required strength cannot be obtained. Further, if the low temperature transformation phase composed of martensite and bainite is less than 10%, the required strength cannot be ensured. On the other hand, if it exceeds 30%, the ductility deteriorates remarkably. Further, the pearlite phase is preferably as small as possible in order to adjust the balance between strength and ductility, and is 10% or less.
Such a final metal structure is achieved by strictly controlling the temperature and cooling rate at each stage in the continuous annealing-hot dip galvanizing line, and accurately controlling the two-phase structure of the material steel sheet at each time point. can do.

Example 1;
A slab having the composition shown in Table 1 was hot-rolled to a plate thickness of 3.6 mm under conditions of a hot rolling finishing temperature of 880 ° C. and a winding temperature of 550 ° C., and then cold-rolled to a plate thickness of 2.0 mm.
After forming an Fe-based plating layer with a plating adhesion amount of 3 g / m ^{2 on} a cold-rolled sheet, annealing was performed at 800 ° C., followed by cooling to 550 ° C. at 10 ° C./second as primary cooling, and then 3 Cooled to 460 ° C at 0 ° C / second. The annealed plate cooled to 460 ° C. was immersed in a molten zinc bath set at 460 ° C., and subsequently alloyed at 460 ° C.

The tensile characteristics of each obtained hot-dip galvanized steel sheet were investigated.
Tensile properties were investigated in accordance with JIS Z2241 using No. 5 test piece described in JIS Z2201 cut out at right angles to the rolling direction.
The results are shown in Table 2.

No. which is an example of the present invention. In Nos. 1 to 7, the tensile strength is as high as 590 MPa or more, and the yield ratio is 70% or less and the low yield ratio is high.
On the other hand, No. which is a comparative example. In No. 8, since the amount of C is small, the tensile strength is as low as 465 MPa, and high strength is not obtained. No. In No. 9, since Mn was added in a large amount exceeding the range of the present invention, the total elongation was remarkably lowered, and the balance between strength and ductility was not good.

Example 2;
The component composition is within the scope of the present invention. Various hot-dip galvanized steel sheets were prepared using steels 1, 4 and 6 with various production conditions changed as shown in Table 3, and the tensile properties of the respective plated steel sheets were investigated by the same method as in Example 1.
The results are shown in Table 4.

Production No. Since the annealing temperature of No. 1 was too high, the volume ratio of austenite was excessive, the volume ratio of pearlite after cooling was too large, and the tensile strength was as low as 600 MPa or less. Production No. Since the annealing temperature of No. 4 was too low, the austenite volume fraction was low, the low-temperature transformation phase contributing to the improvement of strength after cooling was reduced, and the tensile strength was as low as 600 MPa or less.
Production No. In No. 5, since the cooling rate in the primary cooling step was too fast, the ferrite transformation was not sufficiently progressed, many low-temperature transformation phases with low C concentration were formed, the total elongation was low, and the balance between strength and ductility was poor. Production No. In No. 6, the final volume of the primary cooling process was too high, so the ferrite volume fraction was low, the pearlite volume fraction was high after cooling, the total elongation was low, and the balance between strength and ductility was poor. In addition, production No. In No. 7, since the end temperature of the primary cooling process was too low, the volume fraction of austenite was too high, the volume fraction of the low temperature transformation phase was high after cooling, the total elongation was low, and the balance between strength and ductility was poor.

Production No. No. 11 was too fast in the secondary cooling step, so that the ferrite transformation did not proceed sufficiently, many low-temperature transformation phases with low C concentration were formed, the total elongation was low, and the balance between strength and ductility was poor.
On the other hand, those manufactured within the scope of the present invention had an excellent balance between strength and ductility, with tensile strength exceeding 600 MPa and total elongation exceeding 25%.

Claims (4)

  C: 0.03 to 0.18 mass%, Si: 0.1 to 0.5 mass%, Mn: 1.0 to 2.5 mass%, P: 0.03 mass% or less, S: 0.005 After forming a Fe-based plating layer on a steel sheet having a composition comprising the remainder of Fe and inevitable impurities, including a mass% or less, annealing is performed in a ferrite + austenite two-phase region, and the volume fraction of the ferrite phase is 20 to 50%. After cooling to 650 to 500 ° C. at an average cooling rate of 5 to 20 ° C./second as primary cooling, followed by cooling to a galvanizing bath temperature at an average cooling rate of 5 ° C./second or less as secondary cooling. A method for producing a low yield ratio high tension hot dip galvanized steel sheet, characterized in that the volume fraction of the ferrite phase is 50 to 70%, followed by hot dip galvanizing and alloying treatment. The method for producing a low-yield ratio high-tensile hot-dip galvanized steel sheet according to claim 1, wherein the adhesion amount of the Fe-based plating layer is 1 to 6 g / m ² and the annealing temperature is 700 to 900 ° C.   The structure after hot dip galvanizing and alloying treatment and cooling to room temperature is a composite structure having a volume ratio of 60 to 80% ferrite phase, 10 to 30% low temperature transformation phase, and 10% or less pearlite phase. The manufacturing method of the low yield ratio high tension hot-dip galvanized steel sheet according to claim 1 or 2.   The low steel composition according to any one of claims 1 to 3, wherein the composition of the steel sheet further includes one or two of Cr: 0.1 to 0.5 mass% and Mo: 0.03 to 0.3 mass%. Yield ratio high tension hot dip galvanized steel sheet manufacturing method.