KR20130068401A - High carbon hot/cold rolled steel coil and manufactureing method thereof - Google Patents

Abstract

The present invention relates to a post-process omitted high carbon hot rolled steel sheet and a method for manufacturing the same, which can satisfy the quality of the final product even after partially omitting a process after hot rolling.
In the present invention, the present invention includes, in the embodiment, i)% by weight of C: 0.9 to 1.2%, Si: 0.5% or less, Mn: 0.1 to 1.5%, P: 0.05% or less, and S: 0.03% or less. Preparing a high carbon steel composed of Fe and other unavoidable impurities; Ii) reheating the steel and then performing hot rolling in an austenite region where the finishing temperature of hot rolling is equal to or higher than the Ar3 transformation temperature to produce a steel sheet; Iii) rapidly cooling the steel sheet to 520 ° C. to 660 ° C. before the phase transformation starts in a run-out table (ROT); Iii) maintaining the cooling holding temperature uniformly such that the cooled steel sheet undergoes phase transformation at any one of the cooling temperatures; Iii) winding the steel sheet at the cooling holding temperature; provides a method for manufacturing a high carbon hot rolled steel sheet comprising a.

Description

High carbon hot rolled steel sheet, cold rolled steel sheet and manufacturing method thereof {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, a low-cost, high-strength, post-processing high-carbon hot rolled steel sheet capable of satisfying the quality of the final product without partially eliminating the process after hot rolling and its It relates to a manufacturing method.

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 tool steel, spring steel, or mechanical structural steel that requires high strength and hardness because of its high strength and high hardness.

A method for producing high carbon steel for the spring will be described with reference to the manufacturing process diagram shown in the upper part of FIG.

High carbon steels for springs are first manufactured from high carbon steels, followed by hot rolling, pickling and nodular annealing. Then, the first cold rolling, heat treatment and pickling are repeated, followed by the second cold rolling to produce high carbon steel for spring.

The reason for pickling after hot rolling is to remove an oxide layer which is inevitably generated in the initial material manufactured by hot rolling. The reason for performing the spheroidizing annealing is to homogenize the uneven structure of the material by hot rolling and to lower the strength of the material so that the primary cold rolling is possible.

In addition, the primary cold rolling is subjected to the primary cold rolling in advance in order to optimize the reduction ratio of the secondary cold rolling. And the heat treatment process after the first cold rolling is carried out under appropriate heat treatment conditions to obtain the desired quality to determine the microstructure of the final product.

After the heat treatment, it is pickled again to remove the additional oxide layer formed on the surface of the steel, and finally, the secondary cold rolling to make the final product of the desired thickness.

However, the manufacturing method of the high carbon steel for spring as described above has to go through a variety of processes even after hot rolling, there is a problem that takes a very large cost and time due to the cost of each process and the logistics between processes.

It has a fine and uniform fine pearlite structure to provide an excellent high carbon hot rolled steel sheet having high strength and high hardness at the same time.

It provides a method for producing a high carbon hot rolled steel sheet that can form a fine pearlite in the hot rolling process to omit the subsequent heat treatment process.

One embodiment of the present invention includes by weight% C: 0.9 to 1.2%, Si: 0.5% or less, Mn: 0.1-1.5%, P: 0.05% or less, S: 0.03% or less, balance Fe and other unavoidable A high carbon steel made of impurities, including fine pearlite having a lamella structure with an interlayer spacing of 50 to 150 nm between layers of carbides in the microstructure of the steel, and having a lamellar carbide having a thickness of 10 to 30 nm. Provide a steel sheet high carbon hot rolled steel sheet.

It is preferable here that the interlayer spacing between the layered carbides on such fine pearlite has a uniform size within ± 20 nm.

And the average colony (Colony) size of this fine pearlite phase is preferably 1 ~ 5μm.

The volume fraction of the fine pearlite phase is preferably 70% or more, and more preferably, the sum of the volume fraction of the fine pearlite phase and the bainite phase is 90% or more.

And the Vickers hardness of such a hot-rolled steel sheet is preferably 330 ~ 430 HV.

In another embodiment of the present invention, i) by weight% comprises C: 0.9 to 1.2%, Si: 0.5% or less, Mn: 0.1 to 1.5%, P: 0.05% or less, S: 0.03% or less, and the balance Preparing a high carbon steel composed of Fe and other unavoidable impurities; Ii) reheating the steel and then performing hot rolling in an austenite region where the finishing temperature of hot rolling is equal to or higher than the Ar3 transformation temperature to produce a steel sheet; Iii) rapidly cooling the steel sheet to 520 ° C. to 660 ° C. before the phase transformation starts in a run-out table (ROT); Iii) maintaining the cooling holding temperature uniformly such that the cooled steel sheet undergoes phase transformation at any one of the cooling temperatures; Iii) winding the steel sheet at the cooling holding temperature; provides a method for manufacturing a high carbon hot rolled steel sheet comprising a.

In the cooling step of the method of manufacturing a high carbon hot rolled steel sheet, the steel sheet has a phase transformation rate of 10% or less during cooling, and the steel sheet is preferably kept uniformly in the range of 20 ° C. of the cooling holding temperature. A more preferred range of such cooling holding temperature is 5 ° C.

In addition, in the winding step, the phase transformation fraction of the steel sheet is preferably wound at 70% or more.

In the step of maintaining the cooling temperature, the steel sheet passing through the water cooling stand is preferably air cooled at the top and water cooled at the bottom.

In addition, in the hot rolling step, the steel sheet is hot rolled with a thickness of 1.4mm ~ 4.0mm hot carbon steel sheet manufacturing method.

And the cooling rate of the steel sheet in the cooling step is preferably 50 ~ 300 ℃ / sec.

In addition, it is preferable to maintain the steel sheet for 5 seconds to 60 seconds in the step of maintaining the cooling temperature.

Another embodiment of the present invention provides a method for manufacturing a high carbon hot rolled steel sheet, which omits any one or more processes selected from a pickling process, a spheroidization annealing process, and a primary cold rolling process for the wound steel sheet.

Another embodiment of the present invention provides a method for manufacturing a high carbon hot rolled steel sheet further comprising the step of omitting the heat treatment process for the wound steel sheet and cold rolling at a reduction ratio of 70% or more.

Another embodiment of the present invention provides a high carbon cold rolled steel sheet cold rolled high carbon hot rolled steel sheet as described above.

The method of manufacturing a high carbon hot rolled steel sheet according to an embodiment of the present invention has a technical effect of effectively controlling transformation heat generated during phase transformation in a hot rolling process of high carbon steel through a weak cooling pattern of upper air cooling and lower water cooling.

As such, there is a technical effect of effectively controlling the transformation heat generation to produce a uniform fine pearlite in the hot rolling step.

In addition, by controlling the cooling pattern in the hot rolling process, it is possible to prevent a shape defect or a local overcooling caused by the upper cooling to improve the product quality.

The high carbon hot rolled steel sheet manufactured according to an embodiment of the present invention can produce fine pearlite having an interlayer spacing of 50 nm to 150 nm, and thus provide a technical effect of providing an excellent high carbon hot rolled steel sheet having high strength and high hardness at the same time. There is.

In general, a method of adding an expensive alloy element is generally used to increase the strength. In the present invention, by controlling the carbon content and the cooling pattern without additional cost, an excellent high carbon hot rolled steel sheet having both high strength and high hardness can be provided. There is a technical effect that can be.

According to one embodiment of the present invention, a high-carbon hot-rolled steel sheet may produce fine pearlite having an interlayer spacing of 50 nm to 150 nm, and thus may have a technical effect of omitting a heat treatment step in a subsequent manufacturing process.

In addition to the heat treatment process after hot rolling, there is a technical effect that can further omit the subsequent pickling process, the spheroidizing annealing process, and the primary cold rolling.

By making it possible to omit the subsequent manufacturing process step as described above, it is possible to reduce the cost of the subsequent process when producing the product, it is possible to shorten the manufacturing process time.

In addition, there is also an effect that can prevent the environmental pollution occurring in the pickling process and heat treatment process.

1 is a comparative process chart showing a manufacturing process of a high carbon hot rolled steel sheet according to an embodiment of the present invention in comparison with a conventional manufacturing process.
Figure 2 is a photograph showing the shape of a hot rolled steel sheet produced by cooling the upper portion of the steel sheet according to a comparative example of the present invention.
Figure 3 is a microscopic tissue photograph showing the fine pearlite structure of the prepared high carbon hot rolled steel sheet.
4 is an explanatory diagram showing a temperature change and a phase change of a cooling method and a steel sheet according to an embodiment 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. As used herein, the singular forms “a,” “an,” and “the” include plural forms as well, unless the phrases clearly indicate the opposite. As used herein, the term "comprising" embodies a particular characteristic, region, integer, step, operation, element, and / or component, and other specific characteristics, region, integer, step, operation, element, component, and / or group. It does not exclude the presence or addition of.

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 comprises a weight% C: 0.9 ~ 1.2%, Si: 0.5% or less, Mn: 0.1 ~ 1.5%, P: 0.05% or less, S: 0.03% or less , Balance 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 it contains less than 0.9% of carbon (C), the ferrite structure is formed in the hot rolling process or the carbide layer of the pearlite becomes thin, which causes the strength of the structure to be lowered. If the C content is more than 1.2%, the formation of too much cementite cementite in the hot rolling process or the thickening of the pearlite carbide layer results in excessively high strength, which in turn lowers the cold rolling property or the durability of the final product. This causes the lowering. Therefore, it is preferable to contain carbon (C) in 0.9 to 1.2% 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) at 0.5% or less.

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, it is necessary to contain at least 0.1% manganese (Mn) to form MnS. However, excessively high content of manganese (Mn) of 1.5% or more causes a decrease in toughness or delayed phase transformation more than necessary. Therefore, it is preferable to contain manganese (Mn) in 0.1 to 1.5% range.

Next, phosphorus (P) is demonstrated. Phosphorus (P), when its content exceeds 0.05%, segregates at grain boundaries and causes a decrease in toughness. Therefore, it is preferable to control the content of phosphorus (P) to 0.05% or less.

Next, sulfur (S) will be described. When the content of sulfur (S) is more than 0.03%, it precipitates during the manufacturing process to cause embrittlement of the steel. Therefore, it is preferable to control the content of sulfur (S) to 0.03% or less.

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

Hereinafter, a method of manufacturing the high carbon hot rolled steel sheet described above will be described with reference to a manufacturing process diagram of the present invention shown in the lower part of FIG. 1.

First, by weight% C: 0.9-1.2%, Si: 0.5% or less, Mn: 0.1-1.5%, P: 0.05% or less, S: 0.03% or less, and high carbon made of balance Fe and other unavoidable impurities Steels (for example slab form) are produced.

Next, the manufactured steel is reheated and then hot rolled. Hot rolling is preferably performed in the austenite region where the finishing temperature is equal to or higher than the Ar3 transformation temperature. The reason why the finishing temperature of hot rolling is set as follows is as follows.

If the finish temperature of hot rolling is hot rolled below the Ar3 transformation temperature, cornerstone ferrite or cornerstone cementite is formed, which causes the strength and durability of the final structure to be lowered.

Under such conditions, the steel is hot rolled to produce a thin plate having a thickness of 1.4 mm or more and 4.0 mm or less. The reason for limiting the thickness of the hot rolled steel sheet is that if the thickness of the sheet exceeds 4.0mm, sufficient cooling amount cannot be obtained in the subsequent cooling step and temperature holding step, and thus the phase transformation rate cannot be obtained before winding. During the lower cooling step, the temperature deviation in the thickness direction becomes large and a uniform structure cannot be obtained. In addition, when the thickness of the hot rolled steel sheet is less than 1.4mm, the hot rolling load increases, so that the rolling is not good, and when the final product is manufactured after hot rolling, the cold rolling amount decreases due to the reduction in thickness through cold rolling. The strength of the product becomes low.

Next, it is preferable that the thin plate is rapidly cooled to 660 ° C. or more and 660 ° C. or less before the start of phase transformation by controlled cooling in a water-cooling table (ROT; Run-Out Table). The cooling rate at this time is preferably 50 ~ 300 ℃ / sec. And the reason for cooling the thin plate in such a temperature range is as follows.

If the cooling temperature of the thin plate is lower than 520 ˚C, it is not transformed into fine pearlite but a large amount is converted into bainite, which causes the end product's durability. And when the cooling temperature exceeds 660˚C, coarse pearlite is formed, which increases the interlayer spacing between layered carbides, which causes the strength to decrease, and the phase transformation rate is too slow, resulting in incomplete pearlite structure due to incomplete transformation during cooling. Cause.

In addition, in this cooling step, it is necessary to control so that the phase transformation during cooling does not exceed 10%. This is because the phase transformation in the cooling step is not possible to obtain a uniform fine pearlite structure because the phase transformation occurs at a higher temperature than the temperature holding step.

Next, the cooled thin plate is preferably kept uniformly in the range of ± 20 ℃ at any temperature of the cooling temperature section, more preferably kept uniformly in the range of ± 5 ℃. For example, if the thin plate is cooled to 580˚C, which is included in the cooling temperature range of 520˚C ~ 660˚C by cooling, the temperature of the thin plate within the range of 560˚C ~ 600˚C which is ± 20 ℃ of this temperature. It is desirable to maintain.

In the case of high carbon steel, the carbon is contained in the steel so that the temperature of the steel increases due to the transformation heat generation during phase transformation. As described above, when the transformation heat is generated during the phase transformation of the steel sheet, the temperature of the steel sheet rises during air cooling, and thus a uniform structure cannot be obtained.

Therefore, in order to prevent the temperature rise due to transformation heat generation and to maintain the temperature of the steel sheet uniformly, it is necessary to cool the steel sheet. However, if the upper and lower parts of the steel sheet is rapidly cooled in the hot rolling equipment, the temperature is difficult to control, and in some cases, the cooling rate is increased so that the temperature may be lowered, resulting in uneven structure. Therefore, in order to prevent the temperature of the steel sheet from becoming uneven in this way, it is preferable to cool the upper part of the steel sheet being sold by air cooling and the lower part by water cooling.

Thus, the upper part of the cooled steel plate is cooled by air and the lower part thereof is water cooled to suppress the temperature rise caused by the transformation heat generation of the steel sheet, thereby maintaining a constant temperature of the steel sheet to undergo a temperature maintaining step of causing a uniform phase transformation. .

When controlled cooling in this way, only the temperature rise corresponding to the transformation heat is cooled, so that the temperature can be maintained in the range of ± 20 ° C, preferably in the range of ± 5 ° C. As such, by maintaining the temperature of the steel sheet in the phase transformation uniformly, the structure of the steel sheet can be phase-transformed into a uniform fine pearlite structure.

In addition, by cooling the upper portion of the steel sheet, the steel sheet can prevent the temperature variation in the width direction due to the water cooling, and the local subcooling due to the remaining water. For this reason, the material variation of a steel plate can be reduced.

In addition, the widthwise temperature variation and the number of stays due to the upper cooling result in a poor shape of the hot rolled steel sheet. FIG. 2 shows an example of a shape defect in which a hot rolled steel sheet is twisted like a wave when the upper part is cooled. If such a shape is poor, the workability of subsequent processes may be degraded or the quality of a product may be degraded. Thus, control by lower cooling can ultimately improve the quality of the steel product produced using the hot rolled steel sheet.

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 coiling temperature is preferably wound directly at the cooling holding temperature of the steel sheet.

And the phase transformation fraction of the steel sheet at the time of winding the steel sheet should be more than 70%. At this time, if the phase transformation fraction is less than 70%, the phase transformation occurs after winding, and the transformation heat is generated, and the phase transformation temperature is continuously increased to obtain a uniform fine pearlite structure. Moreover, it becomes a cause of winding shape fall by temperature rise and phase transformation. Thus, in order for the phase transformation fraction of a steel plate to be 70% or more, it is preferable to control the cooling temperature holding time of a steel plate to 5 second or more and 60 second or less.

The hot rolled steel sheet manufactured according to the above process can omit all of the following processes, or optionally any one process. Subsequent steps that can be omitted are pickling after hot rolling, spherical annealing, primary cold rolling and heat treatment.

Therefore, in the method of manufacturing high carbon steel according to one embodiment of the present invention, it is preferable to omit the heat treatment step and immediately perform cold rolling on the hot rolled steel sheet manufactured according to the above process.

At this time, the cold rolling of the steel sheet is preferably cold rolling at a reduction ratio of 70% or more. Cold rolling can adjust the reduction ratio according to the required characteristics of the final product to match the thickness of the product and ensure optimal strength and durability.

In the conventional hot rolling process, since a uniform fine pearlite structure could not be obtained, a uniform fine pearlite structure had to be made through a costly heat treatment process which is a post process. However, since the method for manufacturing high carbon steel according to an embodiment of the present invention may form a uniform fine pearlite structure in the hot rolling process step, it is possible to omit a subsequent process and a heat treatment process for forming a fine pearlite structure.

The cold rolled steel sheet manufactured as described above is processed into a desired product through a molding process and then manufactured into a final product through deformation aging.

Hereinafter, the structure of the post-process omitted high carbon hot rolled steel sheet manufactured through the above process will be described.

The structure of the post-process omitted high carbon hot rolled steel sheet is formed of a fine pearlite structure including a lamellar structure having an interlayer spacing between layer carbides of 50 nm to 150 nm. At this time, if the interval between the layered carbides exceeds 150 nm, the soft layer between the carbides becomes wider and the strength is lowered. In addition, when the layered carbide interval is smaller than 50 nm, it causes excessively high strength and low durability.

And the thickness of the carbide forming the lamellae is preferably 10 ~ 30 nm. The thickness of the carbide is related to strength and durability. If the thickness of the carbide exceeds 30 nm, a problem occurs during deformation in a thick hardened layer, which degrades durability. If the thickness of the carbide is smaller than 10 nm, the interval between the carbides is narrowed, which causes the strength to be too high.

The variation of the interval between the layered carbides of the fine pearlite is preferably a uniform size within ~ 20nm compared to the average size. Since the microstructure formed in the hot rolled steel sheet is used in the final product without subsequent heat treatment process, it is necessary to control it uniformly. At this time, when the thickness of the layered carbide exceeds 20 nm compared to the average size, the uniformity of the microstructure is lowered, and the durability of the final product is not satisfied, which causes a failure rate of the product.

In addition, it is preferable that the average colony (particle size) of the fine pearlite is formed to 1 μm to 5 μm. At this time, when the colony size is smaller than 1 μm, the fatigue crack retardation effect is lowered, and when the colony size is larger than 5 μm, the transformation rate is slowed to prevent the phase transformation fraction before winding.

Fig. 3 shows the description of such fine pearlite colonies and the description of the spacing of layered carbides.

In the microstructure of the post-process omitted high-carbon hot-rolled steel sheet, such a fine pearlite phase occupies a volume fraction of 70% or more, and it is preferable that the sum total of the fine pearlite phase and the bainite phase is 90% or more.

Since the fine pearlite in the microstructure plays a role of improving the strength and durability, it is preferable that the fine pearlite phase has a volume fraction of 70% or more, and the bainite phase plays a role of maintaining high strength, so the sum with the fine pearlite phase It is desirable to secure 90% or more.

In addition, in the microstructure of the post-process omitted high-carbon hot-rolled steel sheet, it is preferable that the ferrite phase deteriorating strength and the martensite structure deteriorating durability do not exceed 10%.

And such a post-process omitted high carbon hot rolled steel sheet is preferably Vickers hardness of 330HV to 430HV. Hot rolled steel sheet having such a hardness range can secure the initial strength value necessary to obtain the strength of the final product requiring high strength after subsequent cold rolling.

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>

In order to investigate the microstructure and hardness of the post-process omitted high carbon hot rolled steel sheet, a high carbon steel having a composition shown in Table 1 below was prepared.

division C (wt%) Si (wt%) Mn (wt%) P (wt%) S (wt%) Example 1 0.94 0.19 0.47 0.015 0.006 Example 2 1.06 0.19 0.51 0.015 0.005 Example 3 1.19 0.2 0.49 0.016 0.005 Comparative Example 4 0.79 0.21 0.49 0.015 0.005

A slab having the composition shown in Table 1 was prepared, and the slab was then reheated to 1170 ° C. and hot rolled to prepare a thin plate.

The sheet thickness of the hot rolled steel sheet by hot rolling was 2.0 mm in both the comparative example and the example.

As described above, the hot rolled thin plate was quenched in a water cooling stand and cooled under the conditions shown in Table 2 below, and then controlled to a range of ± 5 ° C at each cooling temperature, and then uniformly maintained. .

As described above, the microstructure and hardness of each thin plate manufactured by varying the transformation temperature were measured, and the results are shown together in Table 2 below. Here, Example 1 of Table 1 corresponds to Comparative Example 1-1, Comparative Example 1-5 and Examples 1-2 to Example 1-4 in Table 2 and Example 2 in Table 1 is Comparative Example 2 in Table 2 Samples corresponding to -1, Comparative Examples 2-5 and Examples 2-2 to 2-4. In addition, Example 3 of Table 1 corresponds to Comparative Example 3-1, Comparative Example 3-5 and Examples 3-2 to Example 3-4 in Table 2 and Comparative Example 4 in Table 1 is Comparative Example 4 in Table 2 Samples corresponding to -1 to Comparative Example 4-3.

division Transformation temperature (℃) Hardness (HV) Layer spacing (nm) Carbide Thickness (nm) Microstructure Comparative Example 1-1 500 ± 5 419 - - Bay knight Examples 1-2 550 ± 5 371 94 14.3 Pearlite Example 1-3 600 ± 5 354 109 16.6 Pearlite Examples 1-4 650 ± 5 331 149 22.7 Pearlite Comparative Example 1-5 700 ± 5 261 261 39.8 Pearlite Comparative Example 2-1 500 ± 5 431 - - Bay knight Example 2-2 550 ± 5 401 71 12.2 Pearlite Example 2-3 600 ± 5 383 100 17.2 Pearlite Examples 2-4 650 ± 5 339 131 22.5 Pearlite Comparative Example 2-5 700 ± 5 284 213 36.6 Pearlite Comparative Example 3-1 500 ± 5 446 - - Bay knight Example 3-2 550 ± 5 422 62 11.9 Pearlite Example 3-3 600 ± 5 395 94 18.1 Pearlite Example 3-4 650 ± 5 353 120 23.1 Pearlite Comparative Example 3-5 700 ± 5 309 188 36.2 Pearlite Comparative Example 4-1 550 ± 5 320 119 15.5 Pearlite Comparative Example 4-2 600 ± 5 303 123 16.0 Pearlite Comparative Example 4-3 650 ± 5 285 165 21.4 Pearlite

As shown in Table 2, the layered spacing between the layered carbides in pearlite tended to increase with increasing temperature, except for Comparative Examples 1-1, 2-1, and 3-1, which showed bainite phase. In particular, Comparative Examples 1-5, 2-5, 3-5 showed a very large layer spacing due to the high transformation temperature of 700 ° C.

In addition, as can be seen in Table 2, the Vickers hardness value was inversely related to the transformation temperature. In Comparative Examples 1-1, 2-1, and 3-1, which have a low transformation temperature of 500 ° C, very high hardness values were observed. This fact lowered the cold rolling property or the strength of the final product after cold rolling was very high. High and low durability is a factor.

On the other hand, Comparative Example 4 shows a somewhat low carbon content of 0.79, and when produced at the transformation temperature of 520 ℃ to 660 ℃ showed a result that the hardness is less than the standard value. This resulted in low hardness because of low carbon content and wide carbide spacing and thin carbide thickness compared with the spacing.

4 is an explanatory view showing a method of cooling a hot rolled thin plate with reference to Example 2-3, a temperature change of the steel sheet, and a change of phase fraction accordingly.

In FIG. 4, reference numeral 1 denotes a control panel displaying a cooling state of the water cooling stand. In this control panel 1, the left roll drawing FDT represents the finish hot rolling roll and the right roll drawing CT represents the take-up roll. 4 denotes the first half of the water cooling stand, and represents a cooling step of rapidly cooling the thin plate after the final hot rolling in the water cooling stand. 4 denotes the second half of the water cooling stand, and shows a temperature holding step of maintaining the temperature of the thin plate cooled after the cooling step as it is in the cooled temperature state.

In FIG. 4, the cooling water injection banks, designated L1 to F16, are installed from the left side to the right side in the water cooling stage in the cooling step 4 and the temperature holding step 5. Each of the cooling water injection banks is composed of a plurality of cooling water injection nozzles, and controls the amount of cooling water injection by controlling the number of cooling water injection nozzles and the number of injection banks as necessary. In Fig. 4, numbers (0 or 1, 2, 4, 6) indicated on the lower line of L1 to F16 and the lowermost line of the control panel 1 indicate the number of nozzles operating in each injection bank.

In this experimental example, the cooling step (4) injects the cooling water at the same time by operating the injection bank in the upper and lower portions of the thin plate (line connecting the finishing hot rolling roll and the winding roll center) passing between the rolls, and maintaining the temperature ( In 5), the cooling water injection bank installed on the upper part of the thin plate does not operate, and only the cooling water bank installed on the lower part of the thin plate is operated to cool only the lower part of the thin plate. The operating conditions of the water cooling stand are the same in both Comparative Examples and Examples of Table 2.

Next, reference numeral 2 will be described with reference to FIG. 4. Reference numeral 2 of FIG. 4 shows the temperature change and the passage time in the water cooling zone for the high carbon thin plate according to Example 2-3. The thin plate of Example 2-3 is cooled from 880 ° C in the cooling stage 4 of the water cooling stand to stop cooling at 600 ° C, and then maintains (6) 600 ° C ± 3 in the temperature holding step (5).

As described above, the high carbon thin plate according to Example 2-3 shows the phase change rate with time of the thin plate shown while passing through the water cooling zone. 4 denotes a phase transformation fraction at the time of winding.

Next, the cold rolling was performed by selecting Comparative Example 1-1 and Example 1-3 in the prepared thin plate.

In order to perform cold rolling, the prepared hot rolled steel sheet was pickled to remove the surface oxide layer. Then, the hot rolled steel sheet was cold rolled at a reduction ratio of 80% to prepare a cold rolled steel sheet having a thickness of 0.4 mm.

As a result of cold rolling under such conditions, the hot rolled steel sheet manufactured according to Comparative Example 1-1 had a problem that the steel sheet itself was cut out due to cracking from the side during cold rolling, and the strength was too high above a certain rolling rate. It was no longer cold rolled up.

However, the hot rolled steel sheet manufactured according to the conditions of Example 1-3 was produced a cold rolled steel sheet of homogeneous quality under the above cold rolling conditions.

Therefore, the cold rolled steel sheet manufactured according to Example 1-3 was molded by a spring. Thus processed products were made of high carbon steel for spring through deformation aging.

As a result of the final product test of the spring-made high carbon steel, the tensile strength was 2230MPa and the durability was over 120,000 times.

Therefore, when hot rolling and cold rolling were carried out according to the embodiment of the present invention, it was confirmed that when manufactured with spring steel, a tensile strength of 2200 MPa or more and a durability of 120,000 times or more, which are required criteria of the final spring steel, can be secured.

As described above, when a uniform fine pearlite structure was formed through hot rolling, it was confirmed that a final product having a desired quality could be obtained without omitting a subsequent manufacturing process such as heat treatment.

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 (20)

It is a high carbon steel material containing C: 0.9 to 1.2%, Si: 0.5% or less, Mn: 0.1 to 1.5%, P: 0.05% or less, S: 0.03% or less, and the balance Fe and other unavoidable impurities. A high carbon hot rolled steel sheet including lamellar fine pearlite having a lamellar structure having an interlayer spacing between layer carbides of 50 to 150 nm in a microstructure of the steel, and having a lamellar thickness of 10 to 30 nm. The method of claim 1,
A high carbon hot rolled steel sheet having a uniform size, wherein the interlayer spacing between the layered carbides on the fine pearlite is within ± 20 nm. The method of claim 1,
The high-carbon hot-rolled steel sheet having an average colony (particle size) of 1 to 5 μm on the fine pearlite phase. The method according to claim 2 or 3,
A high carbon hot rolled steel sheet having a volume fraction of the fine perlite phase of 70% or more. 5. The method of claim 4,
A high carbon hot rolled steel sheet having a sum of volume fractions of the fine pearlite phase and the bainite phase of 90% or more. The method according to any one of claims 1 to 3 and 5,
Vickers hardness of the hot rolled steel sheet is a high carbon hot rolled steel sheet of 330 ~ 430 HV. By weight percent high carbon steels comprising C: 0.9-1.2%, Si: 0.5% or less, Mn: 0.1-1.5%, P: 0.05% or less, S: 0.03% or less, and the balance Fe and other unavoidable impurities Preparing;
Reheating the steel and then performing hot rolling in an austenite region where the finishing temperature of hot rolling is equal to or greater than the Ar3 transformation temperature to produce a steel sheet;
Rapidly cooling the steel sheet to 520 ° C. to 660 ° C. before the phase transformation starts in a run-out table (ROT);
Maintaining a cooling holding temperature uniformly such that the cooled steel sheet undergoes a phase transformation at any one of the cooling temperatures;
Winding the steel sheet at the cooling holding temperature;
Method for producing a high carbon hot rolled steel sheet comprising a. The method of claim 7, wherein
In the cooling step, the steel sheet is a method of manufacturing a high carbon hot rolled steel sheet having a phase transformation rate of 10% or less during cooling. 9. The method of claim 8,
The method of manufacturing a high carbon hot rolled steel sheet at the cooling holding temperature the steel sheet is uniformly maintained in the range ± 20 ℃ of the cooling holding temperature. 9. The method of claim 8,
The method of manufacturing a high carbon hot rolled steel sheet at the cooling holding temperature the steel sheet is uniformly maintained in the range ± 5 ℃ of the cooling holding temperature. 10. The method of claim 9,
The method of manufacturing a high carbon hot rolled steel sheet in which the phase transformation fraction of the steel sheet is wound at 70% or more in the winding step. The method of claim 11,
The method of manufacturing a high-carbon hot rolled steel sheet in which the steel sheet passing through the water cooling stand at the step of maintaining the cooling temperature, the upper portion is cooled by air and the lower portion is cooled by water. 13. The method according to any one of claims 7 to 12,
In the hot rolling step, the steel sheet is hot rolled to a thickness of 1.4mm ~ 4.0mm hot carbon steel sheet manufacturing method. 13. The method according to any one of claims 7 to 12,
Cooling rate of the steel sheet in the cooling step is a method of manufacturing a high carbon hot rolled steel sheet 50 ~ 300 ℃ / sec. 13. The method according to any one of claims 7 to 12,
Method of manufacturing a high carbon hot rolled steel sheet for maintaining the steel sheet for 5 seconds to 60 seconds in the step of maintaining the cooling temperature. 13. The method according to any one of claims 7 to 12,
The wound steel sheet is a method of manufacturing a high carbon hot rolled steel sheet omitting any one or more processes selected from a pickling process, a spheroidizing annealing process and a primary cold rolling process. 13. The method according to any one of claims 7 to 12,
The coiled steel sheet is omitted, the heat treatment step, and the method of manufacturing a high carbon hot rolled steel sheet further comprising the step of cold rolling at a reduction ratio of 70% or more. The method of claim 13,
The coiled steel sheet is omitted, the heat treatment step, and the method of manufacturing a high carbon hot rolled steel sheet further comprising the step of cold rolling at a reduction ratio of 70% or more. A high carbon cold rolled steel sheet cold rolled using the hot rolled steel sheet of any one of claims 1 to 3. A high carbon cold rolled steel sheet manufactured by the manufacturing method of claim 7.

Images