KR101353551B1 - High carbon hot/cold rolled steel coil and manufactureing method thereof - Google Patents

Abstract

The hot rolled structure of the high carbon alloy steel is controlled to distribute the spheroidized particles finely and uniformly after cold rolling and spheroidizing annealing, thereby providing a high carbon steel sheet having excellent formability and excellent final heat treatment.
In the present invention, in the present embodiment, i) by weight% C: 0.39 to 0.43%, Si: 0.10 to 0.35%, Mn: 0.75 to 0.95%, P: 0.02% or less (not including 0%), S : 0.005% or less (0% not included), Cr: 0.90 to 1.1%, Mo: 0.15 to 0.25%, V: 0.01% or less (0% not included), Ti: 0.02% or less (0% N) 0.007% (does not include 0%), to prepare a high carbon slab form consisting of balance Fe and other unavoidable impurities; Ii) reheating the slab above an Ar3 transformation point at a temperature; Iii) roughly rolling the slab and finishing rolling in an austenite region above the Ar3 transformation point to produce a thin plate; Iii) cooling the thin plate at a cooling stage at an initial cooling rate of 20 to 25 ° C./sec and a second stage cooling rate to a cooling rate of 50 to 55 ° C./sec; Iii) finishing cooling the thin plate at a temperature range of 570 ± 10 ° C. and then winding the thin plate in the cooling end temperature range; It provides a method of manufacturing a high carbon steel sheet having excellent moldability.

Description

High carbon steel sheet with excellent formability and manufacturing method {HIGH CARBON HOT / COLD ROLLED STEEL COIL AND MANUFACTUREING METHOD THEREOF}

The present invention relates to a high carbon steel sheet and a method for manufacturing the same, and more particularly, to a high carbon hot rolled steel sheet and a method for manufacturing the same by controlling the hot rolling process to finely and uniformly distribute carbides.

The high carbon steel sheet refers to steel sheet containing 0.3 wt% or more of carbon and its crystal structure having a pearlite crystal phase.

The high carbon steel sheet has high strength and high hardness after the final process. As such, the high carbon steel sheet is used as a cover material for tool steel, spring steel, or shell shell material, which has high strength and high hardness, and thus requires high strength and hardness.

In order to manufacture a high carbon steel plate for such a use, it is good that workability in a subsequent process is favorable. For this purpose, the cooling rate must be controlled in the hot rolling process so that carbides can be finely and uniformly distributed.

However, in order to realize these properties, there is a problem in that the shape of the product is deteriorated by rapid cooling when the bainite phase is formed to form a low temperature structure in the hot rolling process.

In general, high carbon steels are manufactured by hot rolled steel and then subjected to spheroidization annealing to make the final structure into spheroidized cementite. At this time, the finer the spheroidized structure, the better the workability.

In the case of high carbon alloy steel, an alloy element having good hardenability is added to improve physical properties. In this way, when the alloying element is added to the high carbon steel, the nose portion of the heat treatment curve (CCT curve) is moved to the right to make a mechanically excellent steel sheet. In the case of such a high-carbon alloy steel sheet, even when the final product is used, it realizes characteristics such as rust prevention and high strength.

However, the high carbon steel sheet thus manufactured is mechanically processed into the shape of the final product in a subsequent process after cold rolling. At this time, the finer and evenly distributed spheroidized carbide in the structure of the steel sheet, the better the workability.

To this end, the high-carbon steel sheet is pickled and cold rolled to increase its reduction ratio, thereby crushing the pearlite structure in the hot rolled structure and then performing spheroidization annealing.

The hot rolled structure of the high carbon alloy steel is controlled to distribute the spherical particles finely and uniformly after cold rolling and spheroidization annealing, resulting in a high carbon steel sheet having excellent formability and excellent final heat treatment.

After the hot rolling process, by controlling the cooling rate of the steel sheet in multiple stages in the water cooling stage to form the structure of the hot-rolled steel sheet to be the main structure of the bainite to provide a method of manufacturing a high carbon steel sheet without shape defects.

In one embodiment of the present invention, i) C: 0.39 to 0.43%, Si: 0.10 to 0.35%, Mn: 0.75 to 0.95%, P: 0.02% or less (does not include 0%), S: 0.005 % Or less (does not contain 0%), Cr: 0.90 to 1.1%, Mo: 0.15 to 0.25%, V: 0.01% or less (does not contain 0%), Ti: 0.02% or less (does not contain 0%) N: 0.007% (does not include 0%), to prepare a high carbon slab form of balance Fe and other unavoidable impurities; Ii) reheating the slab above an Ar3 transformation point at a temperature; Iii) roughly rolling the slab and finishing rolling in an austenite region above the Ar3 transformation point to produce a thin plate; Iii) cooling the thin plate at a cooling stage at an initial cooling rate of 20 to 25 ° C./sec and a second stage cooling rate to a cooling rate of 50 to 55 ° C./sec; Iii) finishing cooling the thin plate at a temperature range of 570 ± 20 ° C. and then winding the thin plate in the cooling end temperature range; It provides a method of manufacturing a high carbon steel sheet having excellent moldability.

One embodiment of the present invention further comprises the step of cold rolling the wound thin plate with a reduction ratio of 37 ~ 38%.

And one embodiment of the present invention further comprises the step of spheroidizing annealing the cold-rolled steel sheet for less than 8 hours at 600 ℃ ~ Ac1 temperature range.

One embodiment of the present invention as described above is C: 0.39 to 0.43%, Si: 0.10 to 0.35%, Mn: 0.75 to 0.95%, P: 0.02% or less (does not include 0%), S: 0.005% or less (does not contain 0%), Cr: 0.90 to 1.1%, Mo: 0.15 to 0.25%, V: 0.01% or less (does not contain 0%), Ti: 0.02% or less (including 0%) And N: 0.007% (does not contain 0%), and provides a high carbon steel sheet excellent in formability composed of balance Fe and other unavoidable impurities.

The high carbon steel sheet having excellent formability has a fraction of 15% or less of the pearlite phase and the cornerstone ferrite phase, and the rest is composed of the bainite phase.

In addition, the steel sheet is excellent in formability because carbides are uniformly distributed in a structure of 1.3 to 1.7 µm in the structure of the steel sheet after spheroidizing annealing.

The steel sheet has a Young's modulus of 35 to 37 kgf / mm 2, an elongation of 35 to 40%, and a drawing ratio of 1.9 or more.

In the method of manufacturing a high carbon steel sheet according to an embodiment of the present invention, when the steel sheet is cooled in a water cooling zone in a hot rolling process of high carbon steel, the steel sheet manufactured by controlling cooling by changing its cooling rate to an initial stage and a two stage cooling stage There is a technical effect that the shape of the uniform to prevent the generation of defective products.

In addition, the steel sheet according to an embodiment of the present invention can improve the mechanical properties of the high-carbon cold rolled steel sheet for processing through spheroidization annealing. That is, the yield strength of the steel sheet according to an embodiment of the present invention is lower than that of the conventional one can reduce the wear of the tool die during the press working.

In addition, the steel sheet according to an embodiment of the present invention can make the thickness of the hot rolled steel sheet even thinner, thereby lowering the rolling reduction rate during cold rolling, thereby reducing the cost of subsequent processes during production of the product. Process time can be shortened.

1 is a high-carbon steel sheet manufactured according to an embodiment of the present invention is a photograph of the metal structure after the hot rolling process.
Figure 2 is a high-carbon steel sheet prepared according to a comparative example of the present invention is a photograph of the metal structure after the hot rolling process.
Figure 3 is a photograph of the metal structure after the spheroidizing annealing process with a high carbon steel sheet prepared according to an embodiment of the present invention.
Figure 4 is a photograph of the metal structure after the spheroidizing annealing process with a high carbon steel sheet prepared according to a comparative example of the present invention.

The terminology used herein is for the purpose of describing particular embodiments only and is not intended to limit the invention. The singular forms as used herein include plural forms as long as the phrases do not expressly express the opposite meaning thereto. Means that a particular feature, region, integer, step, operation, element and / or component is specified, and that other specific features, regions, integers, steps, operations, elements, components, and / And the like.

Unless defined otherwise, all terms including technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art. Commonly used predefined terms are further interpreted as having a meaning consistent with the relevant technical literature and the present disclosure, and are not to be construed as ideal or very formal meanings unless defined otherwise.

In the present invention, the indication of the chemical composition of the constituent elements means weight percent unless otherwise specified.

Hereinafter, embodiments of the present invention will be described in detail. These embodiments are only for illustrating the present invention, and the present invention is not limited thereto.

High-carbon hot-rolled steel sheet according to an embodiment of the present invention by weight% C: 0.39 ~ 0.43%, Si: 0.10 ~ 0.35%, Mn: 0.75 ~ 0.95%, P: 0.02% or less (does not include 0%) , S: 0.005% or less (0% not included), Cr: 0.90 to 1.1%, Mo: 0.15 to 0.25%, V: 0.01% or less (0% not included), Ti: 0.02% or less (0 %), N: 0.007% (does not contain 0%), and the balance is made of Fe and other unavoidable impurities.

Hereinafter, the reason for limiting the chemical composition of the high carbon hot rolled steel sheet will be described.

First, carbon (C) is demonstrated. Carbon (C) is a component that determines the fraction of high carbon steel microstructure. If the carbon (C) is low, the ferrite structure is produced in the hot rolling process or the carbide layer of the pearlite becomes thin, which causes the strength of the structure to be lowered. In the case of containing a large amount of carbon (C), too much cementite cementite is formed in the hot rolling process, or the carbide layer of pearlite becomes too thick, resulting in excessively high strength. In this case, the cold rolling property is lowered or the durability of the final product is increased. It causes the lowering. Therefore, it is preferable to contain carbon (C) in 0.39 to 0.43% of range.

Next, silicon (Si) will be described. Silicon (Si) not only acts as a deoxidizer but also improves strength. However, as the silicon (Si) content increases, the strength may increase, but scale may be formed on the surface of the steel sheet during the hot rolling process or in a subsequent manufacturing process, thereby degrading the surface quality of the product. Therefore, it is preferable to contain silicon (Si) in 0.10 to 0.35% of range.

Next, manganese (Mn) is demonstrated. Manganese (Mn) can improve the hardenability, improve the strength and combine with sulfur (S) to form MnS can suppress the crack generation due to sulfur (S). Therefore, in order to form MnS, it is necessary to contain 0.75% or more of manganese (Mn). However, containing too much manganese (Mn) is the cause of the toughness or phase transformation is delayed more than necessary. Therefore, it is preferable to contain manganese (Mn) in 0.75 to 0.95% range.

Next, phosphorus (P) is demonstrated. Phosphorus (P), when its content is large, causes segregation at grain boundaries and causes a decrease in toughness. Therefore, it is preferable to control the content of phosphorus (P) to 0.02% or less.

Next, sulfur (S) will be described. When the content of sulfur (S) is large, it precipitates during the manufacturing process to cause embrittlement of the steel. Therefore, it is preferable to control the content of sulfur (S) to 0.005% or less.

Next, chromium (Cr) will be described. Chromium (Cr) improves hardenability and strength and exhibits decarburization and graphitization prevention effects in molten steel during the steelmaking process. However, during heat treatment, the resistance to permanent deformation decreases due to cementite formation and growth promoting effects. Therefore, the content of Cr is limited to 0.9 to 1.1%. If the content of chromium (Cr) is less than 0.9%, sufficient quenchability and decarburization inhibitory effect cannot be expected. If the content of chromium (Cr) exceeds 1.1%, the content is limited in this manner because the hardenability increases more than necessary.

Molybdenum (Mo), vanadium (V) and titanium (Ti) are combined with carbon or nitrogen in the steel to cause precipitation hardening. Therefore, these elements may be added alone or in combination to achieve high strength of the steel sheet even with a small amount of addition through precipitation hardening. However, if the content is more than necessary, the effect tends to be saturated, and the austenite grain size may be reduced, and if the precipitation hardening effect is excessive, brittleness may be increased. Do. Therefore, it is desirable to add 0.15 to 0.25% of molybdenum (Mo), 0.01% or less (V0) of vanadium (V) and 0.02% or less (0%) of titanium (Ti). .

Nitrogen (N) is combined with the precipitation hardening element described above to affect the mechanical properties of the steel. Therefore, the content of nitrogen (N) is preferably limited to 0.007% (not including 0%). If the content of nitrogen is too low, the amount of precipitation of various carbonitrides is small, so the effect of improving strength and resistance to permanent deformation is not sufficient. If the content is too high, the effect is saturated and supersaturated in the matrix structure. Is degraded. Therefore, the content of nitrogen (N) is preferably limited to 0.007% (not including 0%).

In addition, the high-carbon hot-rolled steel sheet according to an embodiment of the present invention, in addition to the above element components, the rest is iron (Fe) and contains other unavoidable impurities.

Hereinafter, a method of manufacturing the above-described high carbon hot rolled steel sheet will be described.

First, C: 0.39 to 0.43%, Si: 0.10 to 0.35%, Mn: 0.75 to 0.95%, P: 0.02% or less (not including 0%), S: 0.005% or less (including 0%) Cr: 0.90 to 1.1%, Mo: 0.15 to 0.25%, V: 0.01% or less (0% not included), Ti: 0.02% or less (0% not included), N: 0.007% (Not including 0%) and produce a high carbon steel (e.g. slab form) consisting of balance Fe and other unavoidable impurities.

Next, the manufactured steel is reheated to an Ar3 transformation point or more and then hot rolled. At this time, the extraction temperature when extracting the final steel in the reheating furnace is 1180 ℃ or more to ensure the surface quality of the final product. In addition, hot rolling is preferably performed in the austenite region in which the temperature of the finish rolling during rough rolling and then finish rolling is equal to or higher than the Ar3 transformation temperature.

The reason for setting the finish rolling temperature of hot rolling in this way is as follows. This is because if the finish rolling temperature of the hot rolling is hot rolled below the Ar3 transformation temperature, the cornerstone ferrite or the cornerstone cementite is formed, which causes the strength and durability of the final structure to be lowered.

Under such conditions, when the steel is hot rolled to produce a thin plate, the extraction temperature at which the thin plate passes through the finishing roll is 870 ± 20 ° C.

Next, the thin plate manufactured in the hot rolling process is cooled by controlled cooling in a run-out table (ROT).

Control cooling in the water cooling zone is controlled by subdividing the cooling conditions into sections when the hot rolled sheet passes through the water cooling zone.

In other words, the initial cooling rate passing through the water cooling zone is relatively slowly controlled cooling to 20 ~ 25 ℃ / sec and then rapidly controlled cooling to 2 ~ 50 ℃ / sec to 50 ~ 55 ℃ / sec to cool at 570 ± 20 ℃ To exit.

The reason for cooling the thin plate by varying the cooling rate in two stages in the water cooling stand is as follows.

If the cooling speed of thin plate is not divided into two stages of cooling rate in the water cooling table, cooling is performed by one rapid cooling, so that the cooling structure is formed by 30% of the cornerstone ferrite and 70% of the pearlite. It is difficult to carry out subsequent work such as pickling, cold rolling and nodular annealing.

However, when the cooling is divided into the initial stage and the second stage, as in one embodiment of the present invention, the cooling structure of the cornerstone ferrite and pearlite represents a fraction of 10 to 15%, and the rest of the phase transformation is made of bainite, the shape of the hot rolled product There is no defect and uniformity, so that the subsequent process can be performed smoothly.

As described above, the thin plate is maintained at a constant temperature to complete phase transformation, and then the steel sheet is wound in a coil state in a winding machine. At this time, the winding temperature is preferably wound directly at 570 ± 20 ℃, the cooling end temperature of the water cooling stage.

The hot rolled steel sheet manufactured according to the above process is subjected to cold rolling at a rolling reduction of 40% or less, preferably 35 to 40%, more preferably 37 to 38%, after the pickling process.

Cold-rolled steel sheet is subjected to spheroidizing annealing for less than 8 hours in the temperature range of 600 ℃ ~ Ac1 and then cooled.

After the spheroidizing heat treatment, the structure of the steel sheet is uniformly distributed carbide, the size of carbide is in the range of 1.3 ~ 1.7㎛ and the physical properties of the steel sheet having such a structure has a Young's modulus of 35 ~ 37 kgf / ㎜, elongation Is about 35 to 40%, and the drawing ratio is 1.9 or more, thus having excellent moldability.

Hereinafter, the present invention will be described in more detail with reference to experimental examples. These experimental examples are only for illustrating the present invention, and the present invention is not limited thereto.

<Experimental Example>

To prepare a high carbon steel having a composition as shown in Table 1 below.

Furtherance
(wt%) C Si Mn P S Cr Mo V Ti N content 0.41 0.25 0.85 0.01 0.004 1.0 0.2 0.001 0.01 0.005

The slabs having the composition shown in Table 1 were prepared, and the slabs were then reheated to 1180 ° C. and then hot rolled to prepare thin plates.

The plate thickness of the hot rolled steel sheet by hot rolling was set to 5.4 mm or 6.3 mm.

As described above, the thin hot rolled sheet was rapidly cooled in a water cooling stand under the conditions shown in Table 2 below, and then the thin plate was wound up.

division
FDT
(℃) ROT cooling rate
(℃ / sec) Coiling
Temperature
(℃) Hot Rolled Steel Thickness
(mm) Perlite fraction
Ferrite fraction
Bainite fraction Early 2nd stage Example 1 870 25 50 to 55 570 5.4 12 4 84 Example 2 870 24 50 to 55 570 5.4 13 5 82 Example 3 870 20 50 to 55 580 5.4 14 7 79 Comparative Example 870 - 50 to 55 624 6.3 70 30 0

As shown in Table 2, in Examples 1 to 3 subjected to the two-stage cooling under the conditions of the embodiment of the present invention, as shown in Fig. 1, the pearlite shows a fraction of 12 to 14% and the salt of ferrite is 4 to 7%. The rest of them show bainite structure, but in the comparative example in which only one cooling was performed, as shown in FIG. 2, the pearlite showed 70% and the cornerstone ferrite as 30%.

Due to the difference in the control cooling method in the water cooling zone, the steel sheet manufactured in the comparative example was difficult to perform the subsequent process due to the poor shape, but in the case of Examples 1 to 3, the shape of the steel sheet was not uniform and was not poor. There was no problem with the subsequent process.

Next, the hot rolled steel sheet prepared according to Example 2 and Comparative Example shown in Table 2 was cold rolled at 37% reduction rate, and then spheroidized annealing for 6 hours at the maximum holding temperature of 720 ° C. in an annealing furnace for 12 hours. Slow cooling.

Table 3 shows the results of measuring the physical properties of the steel sheet subjected to cold rolling and spheroidizing annealing under such conditions.

division YP
(kgf / mm2) TS
(kgf / mm2) EL
(%) Spheroidized carbide size
(탆) Drawing
Ratio Example 2 36.6 53.2 36 1.3 to 1.7 1.9 to 2.3 Comparative Example 40.0 50.8 33 2.0 1.5

When cold rolling and spheroidizing annealing were performed under the above conditions, in Example 2, as shown in FIG. 3, a fine spheroidized structure in which carbides were uniformly distributed without variation was obtained. This resulted in a non-uniform and coarse spheroidized tissue.

Therefore, from this fact, as shown in Table 3, it can be seen that the physical properties of Example 2 are excellent in forming.

Also, it was confirmed that a product having a good shape was formed by forming the remainder in the bainite phase while the fraction of the cornerstone ferrite and pearlite was 10-15% through the controlled cooling of the hot rolling as described above.

While the invention has been shown and described with reference to certain exemplary embodiments thereof, it will be understood by those skilled in the art that various changes and modifications may be made without departing from the scope of the following claims. Those who do it will easily understand.

Claims (7)

By weight% C: 0.39 to 0.43%, Si: 0.10 to 0.35%, Mn: 0.75 to 0.95%, P: 0.02% or less (0% not included), S: 0.005% or less (0% not included) ), Cr: 0.90 to 1.1%, Mo: 0.15 to 0.25%, V: 0.01% or less (0% not included), Ti: 0.02% or less (0% not included), N: 0.007% (0 Manufacturing a high carbon slab form comprising a balance of Fe and other unavoidable impurities;
Reheating the slab to a temperature above Ar3 transformation point;
Roughly rolling the slab and then finishing rolling in an austenite region above an Ar3 transformation point to produce a thin plate;
Cooling the thin plate at a water cooling stage at an initial cooling rate of 20 to 25 ° C./sec, and then cooling the second stage to a cooling rate of 50 to 55 ° C./sec;
Finishing cooling the thin plate at a temperature range of 570 ± 20 ° C. and then winding the thin plate in the cooling end temperature range;
Method for producing a high carbon steel sheet having excellent moldability comprising a. The method of claim 1,
The method of manufacturing a high carbon steel sheet having excellent formability, comprising: cold rolling the wound thin plate to a reduction ratio of 37 to 38%. 3. The method of claim 2,
The method for producing a high carbon steel sheet having excellent formability, further comprising the step of spheroidizing annealing the cold rolled steel sheet in a temperature range of 600 ° C. to Ac 1 for 8 hours or less. By weight% C: 0.39 to 0.43%, Si: 0.10 to 0.35%, Mn: 0.75 to 0.95%, P: 0.02% or less (0% not included), S: 0.005% or less (0% not included) ), Cr: 0.90 to 1.1%, Mo: 0.15 to 0.25%, V: 0.01% or less (0% not included), Ti: 0.02% or less (0% not included), N: 0.007% (0 High carbon steel sheet having a formability of remainder Fe and other unavoidable impurities, and having a fraction of 15% or less of the pearlite phase and the cornerstone ferrite phase and the remainder being the bainite phase. delete 5. The method of claim 4,
The steel sheet is a high carbon steel sheet excellent in formability in which carbides are uniformly distributed in a size of 1.3 to 1.7 μm in the structure of the steel sheet after spheroidizing annealing. The method according to claim 6,
The steel sheet has a high Young's modulus of 35 to 37 kgf / mm 2, an elongation of 35 to 40%, a drawing ratio of 1.9 or more, high carbon steel sheet excellent in formability.

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