JP2018059188A - Abrasion resistant steel sheet and manufacturing method of abrasion resistant steel sheet - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide an abrasion resistant steel sheet having excellent abrasion resistance and flexure processability and a manufacturing method therefor.SOLUTION: There is provided an abrasion resistant steel sheet having a prescribed component composition, hardness at depth of 1 mm from a surface of 460 to 590 HBW 10/3000 as Brinell hardness, volume fraction of martensite at depth of 1 mm from the surface of 90% or more, and dislocation density ρ (m) at depth of 1 mm from the surface and ρwhich is defined by the following (2) formula by using Mf point defined by the following formula (1) and satisfies the following (3) formula. Mf(°C)=410.5-407.3×C-7.3×Si-37.8×Mn-20.5×Cu-19.5×Ni-19.8×Cr-4.5×Mo (1) ρ=15×10×C+2×10-5.74×10×(Mf-100)-1.05×10×(Mf-100) (2) ρ≤ρ(3)SELECTED DRAWING: Figure 2

Description

  TECHNICAL FIELD The present invention relates to a wear-resistant steel plate, and in particular, a wear-resistant steel material excellent in bending workability suitable for use in members of industrial machinery and transportation equipment used in the fields of construction, civil engineering, mining, and the like, and a method for producing the same. About.

  It is known that the wear resistance of a steel material is improved by increasing the hardness. For this reason, for example, steel members that have been subjected to heat treatment such as quenching and have been hardened have been used for members that are subjected to wear due to soil, sand, and the like and require wear resistance.

  For example, Patent Document 1 describes a method of manufacturing a wear-resistant thick steel plate by subjecting a steel material having a predetermined composition to hot rolling to form a thick steel plate and then quenching. According to the method described in the cited document 1, by controlling the contents of C, alloying elements, and N, it has a hardness of 340 HB or more as it is quenched and high toughness, and the weld cold cracking property is improved. It is said that a wear-resistant thick steel plate is obtained.

Patent Document 2 discloses that steel having a predetermined composition is hot-rolled at a temperature of 900 ° C. to Ar ₃ transformation point and a reduction rate of 15% or more, and then directly from the temperature of Ar ₃ transformation point or more. A method for producing wear-resistant steel by quenching is described. According to the technique described in the cited document 2, it is said that wear-resistant steel having high hardness can be easily obtained by controlling the component composition and quenching conditions.

  In the above techniques described in Patent Documents 1 and 2, the wear resistance is improved by increasing the hardness. On the other hand, the demand for wear-resistant steel that excels not only in wear resistance but also in bending workability is increasing due to the application to members of various shapes and the reduction of welding locations.

For such a demand, for example, in Patent Document 3, C: 0.05 to 0.20%, Mn: 0.50 to 2.5%, Al: 0.02 to 2.00% by weight. %, And the martensite area fraction is 5% or more and 50% or less. According to Patent Document 3, the area fraction of martensite is controlled by heating the hot-rolled steel to a ferrite-austenite two-phase region temperature between Ac ₃ point and Ac ₁ point, and then rapidly cooling. As a result, it is said that a wear-resistant steel excellent in workability and weldability can be obtained.

  Patent Document 4 discloses that steel having a predetermined component composition is cooled to an Ms point ± 25 ° C. immediately after hot rolling, and the cooling is interrupted and reheated to an Ms point + 50 ° C. or higher, and then to room temperature. A method of manufacturing a wear-resistant steel sheet for cooling has been proposed. According to the cited document 4, the minimum hardness in the region from the surface of the steel plate obtained by the production method to a depth of 5 mm is 40 HV or more lower than the maximum hardness in the further inner region of the steel plate. It is supposed to improve.

Furthermore, in Patent Document 5, steel having a predetermined component composition with DI of 60 or more is hot-rolled, and then cooled to a temperature range of 400 ° C. or less at an average cooling rate of 0.5 to 2 ° C./s. A method for manufacturing a wear-resistant steel sheet has been proposed. According to Patent Document 5, wherein the wear-resistant steel sheet obtained by the process, and precipitated carbide having an average particle diameter 0.5~50μm more Ti system 400 / mm ² or more, as a result, the heat treatment It is said that a wear-resistant steel having excellent wear resistance and bending workability can be obtained without performing this process.

JP-A 63-169359 JP-A-64-031928 Japanese Patent No. 2864960 Japanese Patent Laid-Open No. 2006-104489 Japanese Patent No. 4899874

  As described in Patent Documents 3 to 5, the conventional method for improving the bendability of wear-resistant steel is to suppress the hardness of the base phase (matrix) of the steel sheet and ensure the bending workability while maintaining the microstructure. This is based on the idea of improving the wear resistance by controlling the amount of carbide or by precipitation of carbides. For this reason, in the above method, it is difficult to sufficiently improve the hardness of the matrix phase, and therefore, there remains a problem in wear resistance.

  An object of the present invention is to solve the above-mentioned problems and to provide a wear-resistant steel sheet having both excellent wear resistance and bending workability. Moreover, an object of this invention is to provide the manufacturing method of the said abrasion-resistant steel plate.

In order to achieve the above-mentioned object, the present inventors have intensively studied various factors that affect the bending workability of wear-resistant steel sheets. As a result, the following findings (1) to (4) were obtained.
(1) The hardness and ductility of the surface layer of the wear-resistant steel plate greatly contribute to the bending workability of the wear-resistant steel plate.
(2) The wear-resistant steel sheet produced by hot rolling and quenching after the hot rolling is further reheated to an appropriate temperature range and tempered, so that tangles of dislocations introduced by quenching can be obtained. As a result, the ductility of the steel sheet surface layer is improved.
(3) According to the method of (2), the bending workability can be improved without reducing the hardness of the base phase that greatly affects the wear resistance.
(4) The effect similar to the above method (2) can be obtained also by a method of rapid heating after quenching or a method of stopping cooling during quenching at a predetermined temperature if the conditions are appropriately selected.

  First, the experimental results on which the present invention is based will be described.

A wear-resistant steel plate was produced by the following procedure. First, in mass%,
C: 0.27%
Si: 0.35%,
Mn: 0.75%
P: 0.005%,
S: 0.002%,
Ti: 0.015%,
Al: 0.03%
Containing Cr: 0.38% and Mo: 0.20%,
A steel slab having a component composition with the balance consisting of Fe and inevitable impurities was prepared as a steel material. The steel slab was heated to 1150 ° C. and hot-rolled to obtain a hot-rolled steel sheet having a thickness of 12 mm. The hot-rolled steel sheet was air-cooled immediately after the end of hot rolling, and then re-heated and quenched. In the reheating quenching, the hot-rolled steel sheet was reheated to a quenching start temperature of 900 ° C. and then cooled to room temperature, which was a quenching stop temperature. After the reheating and quenching, tempering was further performed for 10 minutes at various tempering temperatures.

  Next, a specimen for hardness measurement was collected from the wear-resistant steel plate obtained by the above procedure, and the Brinell hardness was measured in accordance with the provisions of JIS Z 2243 (1998). The measurement was carried out after grinding and removing a region from the steel plate surface to a depth of 1 mm in order to eliminate the influence of the scale and decarburized layer present on the wear-resistant steel plate surface. Therefore, the measured hardness is the surface hardness in a plane having a depth of 1 mm from the steel sheet surface. In the measurement, a tungsten hard sphere having a diameter of 10 mm was used, and the load was 3000 kgf.

  Further, a test piece for measuring dislocation density having a width of 25 mm and a length of 25 mm was taken from the obtained wear-resistant steel plate, and the dislocation density was measured. The measurement was performed after removing a region from the steel plate surface to a depth of 1 mm by grinding, mechanical polishing, and electrolytic polishing in order to remove the influence of the scale and the processed structure existing on the wear-resistant steel plate surface. Therefore, the measured dislocation density is a dislocation density in a plane having a depth of 1 mm from the steel sheet surface. The dislocation density was calculated by obtaining a line profile by X-ray diffraction measurement and analyzing the obtained line profile using the modified Williamson-Hall method and the modified Warren-Averbach method.

  Furthermore, a bending test piece having a width of 50 mm and a length of 150 mm was collected from the obtained steel sheet, and the critical bending radius at a bending angle of 180 ° was measured in accordance with JIS Z 2248. Here, the “limit bending radius” refers to the minimum radius of curvature at which cracks do not occur on the steel sheet surface, and uses the minimum bending radius R (mm) and thickness t (mm) at which cracks do not occur, It can be expressed as R / t.

  The obtained results are shown in FIGS. FIG. 1 shows the relationship between surface hardness (Brinell hardness) and tempering temperature, FIG. 2 shows the relationship between dislocation density and tempering temperature, and FIG. 3 shows the relationship between critical bending radius and tempering temperature. In FIG. 1 to FIG. 3, for comparison, the value of the as-quenched wear-resistant steel plate is indicated by a black circle on the leftmost side of the horizontal axis.

As can be seen from FIGS. 1 to 3, the sample tempered at a tempering temperature lower than (Mf point−100 ° C.) maintains the same surface hardness as that of the as-quenched steel sheet, but the dislocation density is still quenched. As a result, there is no improvement in the critical bending radius. In addition, the sample tempered at a tempering temperature higher than the Mf point has a greatly reduced dislocation density compared to the as-quenched steel sheet, and as a result, the critical bending radius has been greatly improved, but at the same time the surface layer hardness has decreased. Therefore, the wear resistance is inferior. On the other hand, a sample tempered at a tempering temperature not lower than (Mf point−100 ° C.) and not higher than the Mf point has a surface hardness comparable to that of an as-quenched steel sheet, and at the same time from an as-quenched steel sheet Also, the dislocation density is low, and as a result, the critical bending radius is small. Here, the Mf point is a value defined by the following equation (1).
Mf (° C.) = 410.5−407.3 × C−7.3 × Si-37.8 × Mn−20.5 × Cu−19.5 × Ni−19.8 × Cr−4.5 × Mo ... (1)
(However, the element symbol in the above formula (1) is the content of each element expressed in mass%, and the content of the element not contained is 0)

  The present invention has been completed with further studies based on the above findings. That is, the gist of the present invention is as follows.

1. % By mass
C: more than 0.23%, 0.34% or less,
Si: 0.05-1.00%,
Mn: 0.05-2.00%
P: 0.020% or less,
S: 0.050% or less,
Al: 0.100% or less,
Cr: 0.05-0.90%
N: 0.0050% or less, and O: 0.0050% or less,
It has a component composition consisting of the balance Fe and inevitable impurities,
The hardness at a depth of 1 mm from the surface is 460-590 HBW 10/3000 in terms of Brinell hardness,
The volume ratio of martensite at a depth of 1 mm from the surface is 90% or more,
Dislocation density ρ (m ⁻² ) at a depth of 1 mm from the surface, and ρ _u defined by the following equation (2) using the Mf point defined by the following equation (1), the following equation (3) Satisfied, wear-resistant steel plate.
Mf (° C.) = 410.5−407.3 × C−7.3 × Si-37.8 × Mn−20.5 × Cu−19.5 × Ni−19.8 × Cr−4.5 × Mo ... (1)
ρ _u (m ⁻² ) = 15 × 10 ¹⁵ × C + 2 × 10 ¹⁵ −5.74 × 10 ⁹ × (Mf−100) ² −1.05 × 10 ¹¹ × (Mf−100) (2)
ρ ≦ ρ _u (3)
(However, the element symbols in the above formulas (1) and (2) are the contents of each element expressed in mass%, and the contents of the elements not contained are 0)

2. The component composition is mass%,
Nb: 0.005 to 0.025%,
Ti: 0.005-0.030%, and B: 0.0001-0.0018%
2. The wear-resistant steel plate according to 1 above, further comprising one or more selected from the group consisting of:

3. The component composition is mass%,
Cu: 0.01 to 1.00%,
Ni: 0.01 to 5.00%,
Mo: 0.01-2.00%,
V: 0.01 to 1.00%,
W: 0.01-1.00%, and Co: 0.01-1.00%
The wear-resistant steel sheet according to 1 or 2, further containing 1 or 2 or more selected from the group consisting of:

4). The component composition is mass%,
Ca: 0.0005 to 0.0100%,
Mg: 0.0005 to 0.0100%, and REM: 0.0005 to 0.0100%
The wear-resistant steel sheet according to any one of 1 to 3, further containing 1 or 2 or more selected from the group consisting of:

5. The wear-resistant steel sheet according to any one of 1 to 4 above, wherein the density of inclusions and precipitates having an average particle diameter of 500 nm or more at a depth of 1 mm from the surface is 3.0 pieces / mm ² or less.

6). % By mass
C: more than 0.23%, 0.34% or less,
Si: 0.05-1.00%,
Mn: 0.05-2.00%
P: 0.020% or less,
S: 0.050% or less,
Al: 0.100% or less,
Cr: 0.05-0.90%
N: 0.0050% or less, and O: 0.0050% or less,
A steel material having a component composition consisting of the remaining Fe and inevitable impurities is heated to a heating temperature,
Hot-rolling the heated steel material into a hot-rolled steel sheet,
Quenching the hot-rolled steel sheet starts from a quenching start temperature,
The quenching is stopped at a quenching stop temperature equal to or lower than the Mf point defined by the following formula (1), and then the quenched hot-rolled steel sheet is reheated to a tempering temperature, or
Stopping the quenching at the tempering temperature, then air-cooling the quenched hot-rolled steel sheet,
The quenching is direct quenching in which the quenching start temperature is not lower than the Ar ₃ transformation point, or reheating quenching in which the quenching start temperature is not lower than the Ac ₃ transformation point,
The method for producing a wear-resistant steel sheet, wherein the tempering temperature is (Mf point−100 ° C.) or more and Mf point or less.
Mf (° C.) = 410.5-407.3 × C-7.3 × Si-37.8 × Mn-20.5 × Cu-19.5 × Ni-19.8 × Cr-4.5 × Mo ... (1)
(However, the element symbol in the above formula (1) is the content of each element expressed in mass%, and the content of the element not contained is 0)

7). The component composition is mass%,
Nb: 0.005 to 0.025%,
Ti: 0.005-0.030%, and B: 0.0001-0.0018%
7. The method for producing a wear-resistant steel plate according to 6 above, further comprising one or more selected from the group consisting of:

8). The component composition is mass%,
Cu: 0.01 to 1.00%,
Ni: 0.01 to 5.00%,
Mo: 0.01-2.00%,
V: 0.01 to 1.00%,
W: 0.01-1.00%, and Co: 0.01-1.00%
The method for producing a wear-resistant steel sheet according to 6 or 7 above, further comprising 1 or 2 or more selected from the group consisting of:

9. The component composition is mass%,
Ca: 0.0005 to 0.0100%,
Mg: 0.0005 to 0.0100%, and REM: 0.0005 to 0.0100%
The method for producing a wear-resistant steel plate according to any one of 6 to 8, further comprising 1 or 2 selected from the group consisting of:

10. The average particle diameter at a depth of 1 mm from the surface of the wear-resistant steel plate is a density of inclusions and precipitates of 3.0 pieces / mm ² or less, according to any one of the above 6 to 9. A method for producing a wear-resistant steel sheet.

11. It is a manufacturing method of the abrasion-resistant steel plate according to any one of 6 to 10 above,
The quenching is stopped at a quenching stop temperature below the Mf point,
Then, the quenched hot rolled steel sheet is reheated to the tempering temperature,
Furthermore, the manufacturing method of the abrasion-resistant steel plate which hold | maintains the said reheated hot-rolled steel plate at the said tempering temperature.

12 It is a manufacturing method of the abrasion-resistant steel plate according to any one of 6 to 10 above,
The quenching is stopped at a quenching stop temperature below the Mf point,
Next, the method for producing a wear-resistant steel sheet, wherein the quenched hot-rolled steel sheet is reheated to the tempering temperature at an average temperature increase rate of 5 ° C./s or more.

13. It is a manufacturing method of the abrasion-resistant steel plate according to any one of 6 to 10 above,
Stop the quenching at the tempering temperature,
Next, a method for producing a wear-resistant steel sheet, wherein the quenched hot-rolled steel sheet is air-cooled.

  According to the present invention, a wear-resistant steel plate having both bending workability and wear resistance can be easily produced.

  The following a to k are examples of other preferred embodiments of the present invention.

a. % By mass
C: more than 0.23%, 0.34% or less,
Si: 0.05-1.00%,
Mn: 0.50 to 2.00%,
P: 0.020% or less,
S: 0.020% or less,
Al: 0.04% or less,
Cr: 0.15-0.90%,
N: 0.0050% or less, and O: 0.0050% or less,
It has a component composition consisting of the balance Fe and inevitable impurities,
The hardness at a depth of 1 mm from the surface is 460-590 HBW 10/3000 in terms of Brinell hardness,
The volume ratio of martensite at a depth of 1 mm from the surface is 90% or more,
A wear-resistant steel sheet in which dislocation density ρ at a depth of 1 mm from the surface, Mf point defined by the following formula (1), and ρ _u defined by the following formula (2) satisfy the following formula (3).
Mf (° C.) = 410.5−407.3 × C−7.3 × Si-37.8 × Mn−20.5 × Cu−19.5 × Ni−19.8 × Cr−4.5 × Mo ... (1)
ρ _u (m ⁻² ) = 15 × 10 ¹⁵ × C + 2 × 10 ¹⁵ −5.74 × 10 ⁹ × (Mf−100) ² −1.05 × 10 ¹¹ × (Mf−100) (2)
ρ (m ⁻² ) ≦ ρ _u (3)
(However, the element symbols in the above formulas (1) and (2) are the contents of each element expressed in mass%, and the contents of the elements not contained are 0)

b. The component composition is mass%,
Nb: 0.005 to 0.020%,
Ti: 0.010 to 0.017%, and B: 0.0001 to 0.0015%
The wear-resistant steel plate according to the above a, further containing one or more selected from the group consisting of:

c. The component composition is mass%,
Cu: 0.01 to 0.2%,
Ni: 0.01 to 2.0%,
Mo: 0.1 to 0.5%,
V: 0.01 to 0.05%,
W: 0.01-0.05%, and Co: 0.01-0.05%
The wear-resistant steel sheet according to the above a or b, further containing one or more selected from the group consisting of:

d. The component composition is mass%,
Ca: 0.0005 to 0.0040%,
Mg: 0.0005-0.0050%, and REM: 0.0005-0.0080%
The wear-resistant steel sheet according to any one of the above a to c, further containing 1 or 2 or more selected from the group consisting of:

e. % By mass
C: more than 0.23%, 0.34% or less,
Si: 0.05-1.00%,
Mn: 0.50 to 2.00%,
P: 0.020% or less,
S: 0.020% or less,
Al: 0.04% or less,
Cr: 0.15-0.90%,
N: 0.0050% or less, and O: 0.0050% or less,
A steel material having a component composition consisting of the remaining Fe and inevitable impurities is heated to a heating temperature,
Hot-rolling the heated steel material into a hot-rolled steel sheet,
Quenching the hot-rolled steel sheet starts from a quenching start temperature,
The quenching is stopped at a quenching stop temperature equal to or lower than the Mf point defined by the following formula (1), and then the quenched hot-rolled steel sheet is reheated to a tempering temperature, or
Stopping the quenching at the tempering temperature, then air-cooling the quenched hot-rolled steel sheet,
The quenching is direct quenching in which the quenching start temperature is not lower than the Ar ₃ transformation point, or reheating quenching in which the quenching start temperature is not lower than the Ac ₃ transformation point,
The method for producing a wear-resistant steel sheet, wherein the tempering temperature is (Mf point−100 ° C.) or more and Mf point or less.
Mf (° C.) = 410.5-407.3 × C-7.3 × Si-37.8 × Mn-20.5 × Cu-19.5 × Ni-19.8 × Cr-4.5 × Mo ... (1)
(However, the element symbol in the above formula (1) is the content of each element expressed in mass%, and the content of the element not contained is 0)

f. The component composition is mass%,
Nb: 0.005 to 0.020%,
Ti: 0.010 to 0.017%, and B: 0.0001 to 0.0015%
The method for producing a wear-resistant steel sheet according to e, further comprising one or more selected from the group consisting of:

g. The component composition is mass%,
Cu: 0.01 to 0.2%,
Ni: 0.01 to 2.0%,
Mo: 0.1 to 0.5%,
V: 0.01 to 0.05%,
W: 0.01-0.05%, and Co: 0.01-0.05%
The method for producing a wear-resistant steel sheet according to the above e or f, further comprising 1 or 2 or more selected from the group consisting of:

h. The component composition is mass%,
Ca: 0.0005 to 0.0040%,
Mg: 0.0005-0.0050%, and REM: 0.0005-0.0080%
The method for producing a wear-resistant steel sheet according to any one of the above e to g, further comprising one or more selected from the group consisting of:

i. It is a manufacturing method of the abrasion-resistant steel plate according to any one of the above e to h,
The quenching is stopped at a quenching stop temperature below the Mf point,
Then, the quenched hot rolled steel sheet is reheated to the tempering temperature,
Furthermore, the manufacturing method of the abrasion-resistant steel plate which hold | maintains the said reheated hot-rolled steel plate at the said tempering temperature.

j. It is a manufacturing method of the abrasion-resistant steel plate according to any one of the above e to h,
The quenching is stopped at a quenching stop temperature below the Mf point,
Next, the method for producing a wear-resistant steel sheet, wherein the quenched hot-rolled steel sheet is reheated to the tempering temperature at an average temperature increase rate of 5 ° C./s or more.

k. It is a manufacturing method of the abrasion-resistant steel plate according to any one of the above e to h,
Stop the quenching at the tempering temperature,
Furthermore, the manufacturing method of an abrasion-resistant steel plate which air-cools the said hot-rolled steel plate quenched.

It is a graph which shows the relationship between surface hardness and tempering temperature. It is a graph which shows the relationship between a dislocation density and tempering temperature. It is a graph which shows the relationship between a limit bending radius and tempering temperature.

[Ingredient composition]
Next, a method for carrying out the present invention will be specifically described. In the present invention, it is important that the wear-resistant steel plate and the steel material used for manufacturing the steel plate have the above component composition. First, the reason why the composition of steel is limited as described above in the present invention will be described. In addition, "%" regarding a component composition shall mean "mass%" unless there is particular notice.

C: More than 0.23% and not more than 0.34% C is an element having an action of increasing the hardness of the matrix phase and improving the wear resistance. In order to acquire the said effect, C content shall be more than 0.23%. The C content is preferably 0.26% or more. On the other hand, when the C content exceeds 0.34%, the hardness of the matrix phase is excessively increased, and the bending workability is remarkably deteriorated. Therefore, the C content is set to 0.34% or less. The C content is preferably 0.31% or less.

Si: 0.05-1.00%
Si is an element that acts as a deoxidizer. Moreover, Si has the effect | action which dissolves in steel and raises the hardness of a base phase by solid solution strengthening. In order to obtain these effects, the Si content is set to 0.05% or more. The Si content is preferably 0.10% or more, and more preferably 0.20% or more. On the other hand, when the Si content exceeds 1.00%, problems such as a decrease in ductility and toughness and an increase in the amount of inclusions occur. Therefore, the Si content is set to 1.00% or less. The Si content is preferably 0.80% or less, more preferably 0.60% or less, and even more preferably 0.40% or less.

Mn: 0.05 to 2.00%
Mn is an element having an action of increasing the hardness of the matrix phase and improving the wear resistance. In order to acquire the said effect, Mn content shall be 0.05% or more. The Mn content is preferably 0.25% or more, and more preferably 0.50% or more. On the other hand, if the Mn content exceeds 2.00%, the hardness becomes too high, so that the bending workability is lowered. Therefore, the Mn content is 2.00% or less. The Mn content is preferably 1.80% or less, and more preferably 1.60% or less.

P: 0.020% or less P is an element contained as an unavoidable impurity, and causes segregation at a grain boundary to become a starting point of fracture, or forms a phosphide to lower bending workability. ,Adversely affect. Therefore, the P content is 0.020% or less. The P content is preferably 0.015% or less. On the other hand, since it is desirable to make the P content as low as possible, the lower limit of the P content is not particularly limited and may be 0%. Usually, P is an element inevitably contained in the steel as an impurity. Therefore, it may be more than 0% industrially. Moreover, since excessive reduction causes the refining cost to rise, the P content is preferably set to 0.001% or more.

S: 0.050% or less S is an element contained as an unavoidable impurity and is present in steel as sulfide inclusions such as MnS, and has an adverse effect such as becoming a starting point of fracture. . Therefore, the S content is 0.050% or less. The S content is preferably 0.020% or less. On the other hand, since it is desirable to make the S content as low as possible, the lower limit of the S content is not particularly limited and may be 0%, but usually S is an element inevitably contained in the steel as an impurity. Therefore, it may be more than 0% industrially. Moreover, since excessive reduction leads to an increase in refining costs, the S content is preferably set to 0.0005% or more.

Al: 0.100% or less Al is an element that acts as a deoxidizer and has the effect of refining crystal grains. In order to obtain these effects, the Al content is preferably 0.01% or more. On the other hand, if the Al content exceeds 0.100%, the oxide inclusions increase and the cleanliness decreases. The decrease in cleanliness causes a deterioration in surface properties due to an increase in surface defects and a decrease in bending workability. Therefore, the Al content is 0.100% or less. The Al content is preferably 0.050% or less, more preferably 0.040% or less, and even more preferably 0.030% or less.

Cr: 0.05-0.90%
Cr is an element that has the effect of increasing the hardness of the matrix phase and improving the wear resistance. In order to acquire the said effect, Cr content shall be 0.05% or more. The Cr content is preferably 0.15% or more, and more preferably 0.25% or more. On the other hand, if the Cr content exceeds 0.90%, the hardness becomes too high, so that the bending workability is lowered. Therefore, the Cr content is set to 0.90% or less. The Cr content is preferably 0.85% or less, and more preferably 0.80% or less.

O: 0.0050% or less O is an element contained as an unavoidable impurity and is present in steel as inclusions such as oxides, and is an element that has an adverse effect, such as becoming a starting point of fracture. A content of 0.0050% or less is acceptable. The O content is preferably 0.0040% or less, and more preferably 0.0030% or less. On the other hand, the lower limit of the O content is not particularly limited and may be 0%. However, since O is an element that is inevitably contained in steel as an impurity, it is industrially more than 0%. It's okay.

N: 0.0050% or less N is an element contained as an unavoidable impurity and exists in steel as inclusions such as nitrides, and is an element having an adverse effect such as becoming a starting point of fracture. A content of 0.0050% or less is acceptable. The N content is preferably 0.0040% or less, and more preferably 0.0030% or less. On the other hand, the lower limit of the N content is not particularly limited and may be 0%. However, since N is an element inevitably contained in steel as an impurity, it is industrially more than 0%. It's okay.

  The wear-resistant steel plate and steel material in one embodiment of the present invention are composed of the above components, the remaining Fe and unavoidable impurities.

  The above is the basic component composition in the present invention, but in other embodiments, the component composition is arbitrarily selected from Nb: 0.005 to 0.025%, Ti: 0.005 to 0.030%, and B : 1 or 2 or more selected from the group consisting of 0.0001 to 0.0018% can be further contained.

Nb: 0.005 to 0.025%
Nb is an element that increases the hardness of the matrix phase and contributes to improvement of wear resistance. When adding Nb, in order to acquire the said effect, Nb content shall be 0.005% or more. The Nb content is preferably 0.007% or more. On the other hand, when the Nb content exceeds 0.025%, a large amount of NbC is precipitated, and the bending workability is lowered. Therefore, when adding Nb containing, Nb content shall be 0.025% or less. The Nb content is preferably 0.023% or less, more preferably 0.021% or less, further preferably 0.020% or less, and most preferably 0.019% or less. .

Ti: 0.005-0.030%
Ti is an element that has a strong tendency to form nitrides and has an action of fixing N and reducing solute N. Therefore, the toughness of the base material and the welded portion can be improved by adding Ti. Moreover, when both Ti and B are added, precipitation of BN is suppressed when Ti fixes N, and as a result, the effect of improving the hardenability of B is promoted. In order to obtain these effects, when adding Ti, the Ti content is set to 0.005% or more. The Ti content is preferably 0.010% or more, and more preferably 0.012% or more. On the other hand, when the Ti content exceeds 0.030%, a large amount of TiC is precipitated, and the bending workability is lowered. Therefore, when Ti is contained, the Ti content is set to 0.030% or less. The Ti content is preferably 0.025% or less, more preferably 0.020% or less, and still more preferably 0.017% or less.

B: 0.0001 to 0.0018%
B is an element having an effect of significantly improving the hardenability even when added in a small amount. Therefore, the addition of B can promote the formation of martensite and can further improve the wear resistance. In order to acquire the said effect, when adding B, B content shall be 0.0001% or more. The B content is preferably 0.0005% or more, and more preferably 0.0010% or more. On the other hand, when the B content exceeds 0.0018%, a large amount of inclusions such as borides are produced, which causes adverse effects such as occurrence of fracture. Therefore, when adding B, B content shall be 0.0018% or less. The B content is preferably 0.0016% or less, more preferably 0.0015% or less, and even more preferably 0.0014% or less.

  Moreover, in other embodiment of this invention, the said component composition is arbitrarily Cu: 0.01-1.00%, Ni: 0.01-5.00%, Mo: 0.01-2.00. %, V: 0.01 to 1.00%, W: 0.01 to 1.00%, and Co: 0.01 to 1.00%, or one or more selected from the group consisting of 0.01 to 1.00% be able to.

Cu: 0.01 to 1.00%
Cu is an element having an effect of improving the hardenability, and can be arbitrarily added to improve the hardness inside the steel plate. When adding Cu, in order to acquire the said effect, Cu content shall be 0.01% or more. On the other hand, if the Cu content exceeds 1.00%, the weldability is deteriorated and the alloy cost is increased. Therefore, when adding Cu, Cu content is made 1.00% or less. The Cu content is preferably 0.50% or less, and more preferably 0.20% or less.

Ni: 0.01-5.00%
Ni is an element having an effect of improving hardenability like Cu, and can be arbitrarily added in order to improve the hardness inside the steel plate. When adding Ni, in order to acquire the said effect, Ni content shall be 0.01% or more. On the other hand, if the Ni content exceeds 5.00%, weldability is deteriorated and alloy costs are increased. Therefore, when adding Ni, the Ni content is set to 5.00% or less. The Ni content is preferably 3.00% or less, and more preferably 2.00% or less.

Mo: 0.01 to 2.00%
Mo is an element having an effect of improving the hardenability like Cu, and can be arbitrarily added in order to improve the hardness inside the steel plate. When adding Mo, in order to acquire the said effect, Mo content shall be 0.01% or more. The Mo content is preferably 0.1% or more. On the other hand, if the Mo content exceeds 2.00%, weldability is deteriorated and alloy costs are increased. Therefore, when adding Mo, Mo content is made 2.00% or less. The Mo content is preferably 1.00% or less, and more preferably 0.50% or less.

V: 0.01-1.00%
V is an element having an effect of improving the hardenability like Cu, and can be arbitrarily added to improve the hardness inside the steel plate. When adding V, in order to acquire the said effect, V content shall be 0.01% or more. On the other hand, if the V content exceeds 1.00%, weldability is deteriorated and alloy costs are increased. Therefore, when V is added, the V content is 1.00% or less. The V content is preferably 0.50% or less, more preferably 0.25% or less, and even more preferably 0.05% or less.

W: 0.01-1.00%
W is an element having the effect of improving the hardenability like Cu, and can be optionally added to improve the hardness inside the steel plate. When adding W, in order to acquire the said effect, W content shall be 0.01% or more. On the other hand, if the W content exceeds 1.00%, weldability is deteriorated and alloy costs are increased. Therefore, when adding W, W content shall be 1.00% or less. The W content is preferably 0.50% or less, more preferably 0.25% or less, and even more preferably 0.05% or less.

Co: 0.01-1.00%
Co is an element having an effect of improving the hardenability like Cu, and can be arbitrarily added to improve the hardness inside the steel sheet. When Co is added, the Co content is 0.01% or more in order to obtain the above effect. On the other hand, if the Co content exceeds 1.00%, the weldability is deteriorated and the alloy cost is increased. Therefore, when adding Co, the Co content is set to 1.00% or less. The Co content is preferably 0.50% or less, more preferably 0.25% or less, and even more preferably 0.05% or less.

Moreover, in other embodiment of this invention, the said component composition is Ca: 0.0005-0.0100%, Mg: 0.0005-0.0100%, and REM: 0.0005-0. 0100%
1 or 2 or more selected from the group consisting of can further be contained.

Ca: 0.0005 to 0.0100%
Ca is an element having an action of binding to S and suppressing the formation of MnS or the like that extends long in the rolling direction. Therefore, by adding Ca, the form can be controlled so that the sulfide inclusions have a spherical shape, and the toughness of the welded portion and the like can be improved. In order to acquire the said effect, when adding Ca, Ca content shall be 0.0005% or more. On the other hand, if the Ca content exceeds 0.0100%, the cleanliness of the steel decreases. The decrease in cleanliness causes a deterioration in surface properties due to an increase in surface defects and a decrease in bending workability. Therefore, when adding Ca, it is set as Ca content 0.0100% or less. The Ca content is preferably 0.0050% or less, and more preferably 0.0040% or less.

Mg: 0.0005 to 0.0100%
Mg, like Ca, is an element that binds to S and suppresses the formation of MnS or the like that extends long in the rolling direction. Therefore, by adding Mg, it is possible to control the form so that the sulfide inclusions have a spherical shape and improve the toughness of the welded portion and the like. In order to acquire the said effect, when adding Mg, Mg content shall be 0.0005% or more. On the other hand, when the Mg content exceeds 0.0100%, the cleanliness of the steel decreases. The decrease in cleanliness causes a deterioration in surface properties due to an increase in surface defects and a decrease in bending workability. Therefore, when adding Mg, Mg content shall be 0.0100% or less. The Mg content is preferably 0.0060% or less, and more preferably 0.0050% or less.

REM: 0.0005 to 0.0100%
REM (rare earth metal) is an element having an effect of suppressing the formation of MnS or the like which is bonded to S and extends long in the rolling direction, like Ca and Mg. Therefore, by adding REM, it is possible to control the form so that the sulfide inclusions have a spherical shape and to improve the toughness of the welded portion. In order to acquire the said effect, when adding REM, REM content shall be 0.0005% or more. On the other hand, when the REM content exceeds 0.0100%, the cleanliness of the steel decreases. The decrease in cleanliness causes a deterioration in surface properties due to an increase in surface defects and a decrease in bending workability. Therefore, when adding REM, REM content shall be 0.0100% or less. The REM content is preferably 0.0080% or less, and more preferably 0.0060% or less.

In other words, the wear-resistant steel plate and the steel material used for manufacturing the same in the present invention can have the following component composition.
% By mass
C: more than 0.23%, 0.34% or less,
Si: 0.05-1.00%,
Mn: 0.05-2.00%
P: 0.020% or less,
S: 0.050% or less,
Al: 0.100% or less,
Cr: 0.05-0.90%
N: 0.0050% or less,
O: 0.0050% or less,
Optionally, one or more selected from the group consisting of Nb: 0.005-0.025%, Ti: 0.005-0.030%, and B: 0.0001-0.0018%,
Optionally, Cu: 0.01-1.00%, Ni: 0.01-5.00%, Mo: 0.01-2.00%, V: 0.01-1.00%, W: 0 1 or more selected from the group consisting of 0.01 to 1.00% and Co: 0.01 to 1.00%,
Optionally, one or more selected from the group consisting of Ca: 0.0005-0.0100%, Mg: 0.0005-0.0100%, and REM: 0.0005-0.0100%, and the balance A component composition consisting of Fe and inevitable impurities.

[surface hardness]
Brinell hardness: 460-590 HBW 10/3000
In addition to having the above component composition, the wear-resistant steel sheet of the present invention has a Brinell hardness of 460 to 590 HBW 10/3000 at a depth of 1 mm from the surface. The reason for limiting the surface hardness to the above range will be described below.

  The wear resistance of the steel sheet can be improved by increasing the hardness of the surface layer of the steel sheet. When the hardness of the steel sheet surface layer is less than 460 HBW in terms of Brinell hardness, sufficient wear resistance cannot be obtained. Therefore, the hardness of the steel sheet surface layer portion is set to 460 HBW or more in terms of Brinell hardness. On the other hand, if the hardness of the steel sheet surface layer portion exceeds 590 HBW in terms of Brinell hardness, bending workability deteriorates. Therefore, the hardness of the steel sheet surface layer portion is set to 590 HBW or less in terms of Brinell hardness. The “hardness in the surface layer of the steel sheet” herein refers to the Brinell hardness at a position 1 mm deep from the surface of the wear-resistant steel sheet. The Brinell hardness is a value (HBW 10/3000) measured using a tungsten hard sphere having a diameter of 10 mm and a load of 3000 kgf. The Brinell hardness can be measured by the method described in the examples.

[Microstructure]
Martensite volume ratio: 90% or more In the present invention, the volume ratio of martensite at a depth of 1 mm from the surface of the wear-resistant steel sheet (hereinafter simply referred to as “volume ratio of martensite”) is 90% or more. When the volume ratio of martensite is less than 90%, the hardness of the base structure of the steel sheet is lowered, so that the wear resistance is deteriorated. Therefore, the volume ratio of martensite is 90% or more. The remaining structure other than martensite is not particularly limited, but one or more other structures such as ferrite, pearlite, austenite, and bainite structure may be present. On the other hand, since the higher the volume ratio of martensite, the better, the upper limit of the volume ratio is not particularly limited, and may be 100%. In addition, let the volume ratio of the said martensite be the value in the position of the depth of 1 mm from the surface of an abrasion-resistant steel plate. The volume ratio of the martensite can be measured by the method described in the examples.

  In addition, the martensite in this invention shall refer to the martensite which is not tempered martensite, ie, the martensite which cementite does not precipitate. By adopting the manufacturing conditions described later and setting the tempering temperature to (Mf point−100 ° C.) or higher and Mf point or lower, a microstructure with a volume ratio of martensite that is not tempered martensite being 90% can be obtained. .

[Dislocation density]
Furthermore, in the present invention, the dislocation density ρ (m ⁻² ) at a depth of 1 mm from the surface of the wear-resistant steel plate and the Mf point defined by the above-described equation (1) are defined by the following equation (2). Ρ _u satisfies the following expression (3).
ρ _u = 15 × 10 ¹⁵ × C + 2 × 10 ¹⁵ −5.74 × 10 ⁹ × (Mf−100) ² −1.05 × 10 ¹¹ × (Mf−100) (2)
ρ ≦ ρ _u (3)
(However, the element symbol in the above formula (2) is the content of each element expressed in mass%, and the content of the element not contained is 0)

The dislocation density of the steel sheet is affected by the carbon concentration and the temperature conditions (for example, tempering temperature) at the time of manufacturing the steel sheet. If the dislocation density ρ is larger than ρ _u , the ductility of the surface layer of the wear-resistant steel plate is equivalent to that in the as-quenched state, and bending workability is not improved. Therefore, the dislocation density ρ is set to ρ _u or less. On the other hand, the lower the dislocation density, the better. Therefore, the lower limit is not particularly limited, but is usually 1.0 × 10 ¹⁵ or more. The dislocation density is a value at a position 1 mm deep from the surface of the wear-resistant steel plate.

[Density of inclusions and precipitates]
Inclusion / precipitate density: 3.0 pieces / mm ² or less The density of inclusions and precipitates depends on the steel sheet components such as Al, N, and O, and the temperature conditions during the production of the steel sheet (eg, heating temperature). Affected by. The density of inclusions / precipitates having an average particle size of 500 nm or more at a depth of 1 mm from the surface of the wear-resistant steel sheet (hereinafter simply referred to as “inclusions / precipitate density”) is 3.0 pieces / mm ² or less. By doing so, the starting point of the crack at the time of a bending process can be reduced, and bending workability can further be improved. Therefore, the density of the inclusions / precipitates is preferably 3.0 pieces / mm ² or less. On the other hand, the lower the density of inclusions / precipitates, the better. Therefore, the lower limit is not particularly limited, but excessive reduction leads to an increase in the refining cost, so 0.1 / mm ² or more is preferable.

[Thickness]
The plate thickness of the wear-resistant steel plate of the present invention is not particularly limited and may be any thickness, but is preferably 4 to 50 mm from the viewpoint of manufacturing.

[Production method]
Next, the manufacturing method of the abrasion-resistant steel plate in one Embodiment of this invention is demonstrated. The wear-resistant steel plate of the present invention can be produced by heating and hot rolling a steel slab having the above-described component composition, and then performing heat treatment including quenching under the conditions described later.

[Steel material]
Although the manufacturing method of the said steel raw material is not specifically limited, For example, the molten steel which has the above-mentioned composition can be melted by a conventional method, and can be manufactured by casting. The melting can be performed by an arbitrary method such as a converter, electric furnace, induction furnace or the like. In addition, the casting is preferably performed by a continuous casting method from the viewpoint of productivity, but can also be performed by an ingot-decomposing and rolling method. As the steel material, for example, a steel slab can be used.

[heating]
The obtained steel material is heated to a heating temperature prior to hot rolling. The heating may be performed after once cooling a steel material obtained by a method such as casting, or the obtained steel material can be directly subjected to the heating without cooling.

  The heating temperature is not particularly limited, but if the heating temperature is less than 900 ° C., the deformation resistance of the steel material is high, so the load on the rolling mill in hot rolling increases and it is difficult to perform hot rolling. It may become. Therefore, the heating temperature is preferably 900 ° C. or higher, more preferably 950 ° C. or higher, and further preferably 1100 ° C. or higher. On the other hand, if the heating temperature is higher than 1250 ° C., the oxidation of the steel becomes remarkable and the loss due to the oxidation increases, resulting in a decrease in yield. Therefore, the heating temperature is preferably 1250 ° C. or less, more preferably 1200 ° C. or less, and further preferably 1150 ° C. or less.

[Hot rolling]
Next, the heated steel material is hot-rolled to obtain a hot-rolled steel sheet. The conditions for the hot rolling are not particularly limited, and can be performed according to a conventional method. However, if the rolling temperature is less than 850 ° C., the deformation resistance of the steel material is high, so the load on the rolling mill in hot rolling increases, and it may be difficult to perform hot rolling. Therefore, the rolling temperature is preferably 850 ° C. or higher, and more preferably 900 ° C. or higher. On the other hand, if the rolling temperature is higher than 1000 ° C., the oxidation of the steel becomes remarkable due to the high temperature, and the loss due to the oxidation increases, resulting in a decrease in yield. Therefore, the rolling temperature is preferably 1000 ° C. or less, and more preferably 950 ° C. or less.

[Hardening]
Next, the obtained hot-rolled steel sheet is quenched from the quenching start temperature to the quenching stop temperature. The quenching may be performed by either direct quenching (DQ) or reheat quenching (RQ). Moreover, the cooling method in the quenching is not particularly limited, but it is preferably performed by water cooling. Here, the “quenching start temperature” is the surface temperature of the steel sheet at the start of quenching. The “quenching start temperature” may be simply referred to as “quenching temperature”. The “quenching stop temperature” is the surface temperature of the steel plate at the end of quenching. For example, when quenching is performed by water cooling, the temperature at the start of water cooling is set as “quenching start temperature”, and the temperature at the end of water cooling is set as “quenching stop temperature”.

(Direct quenching)
When the quenching is performed by direct quenching, the hot rolled steel sheet is quenched without reheating after the hot rolling is completed. At that time, the said quenching start temperature than the Ar ₃ transformation point. This is to obtain a martensite structure by quenching from the austenite state. If the quenching start temperature is less than the Ar ₃ transformation point, the steel sheet cannot be sufficiently hardened because of sufficient quenching. As a result, the wear resistance of the finally obtained steel sheet is lowered. On the other hand, the upper limit of the quenching start temperature in direct quenching is not particularly limited, but is preferably 950 ° C. or lower. The quenching stop temperature will be described later.

The Ar ₃ transformation point can be obtained by the following equation (4), for example.
Ar ₃ (° C.) = 910-273 × C-74 × Mn-57 × Ni-16 × Cr-9 × Mo-5 × Cu (4)
(However, each element symbol in the formula (4) is the content of each element expressed in mass%, and the content of the element not contained is 0)

(Reheating and quenching)
When the quenching is performed by reheating and quenching, after the hot rolling is finished, the hot rolled steel sheet is reheated and then quenched. At that time, the said quenching start temperature Ac ₃ transformation point or more. This is to obtain a martensite structure by quenching from the austenite state. When the quenching start temperature is less than the Ac ₃ transformation point, the steel sheet cannot be sufficiently hardened because the steel sheet is not sufficiently hardened. As a result, the wear resistance of the finally obtained steel sheet is lowered. On the other hand, the upper limit of the quenching start temperature in the reheating quenching is not particularly limited, but is preferably 950 ° C. or less. The quenching stop temperature will be described later.

Note that the Ac ₃ transformation point can be obtained by the following equation (5), for example.
Ac ₃ (° C.) = 912.0-230.5 × C + 31.6 × Si-20.4 × Mn-39.8 × Cu-18.1 × Ni-14.8 × Cr + 16.8 × Mo (5) )
(However, each element symbol in the formula (5) is the content of each element expressed in mass%, and the content of the element not contained is 0)

(Average cooling rate)
The cooling rate in the quenching is not particularly limited, and can be an arbitrary value as long as it is a cooling rate at which a martensite phase is formed. For example, the average cooling rate between the start of quenching and the quenching stop is preferably 25 to 70 ° C./s, and more preferably 30 to 60 ° C./s. In addition, let the said average cooling rate be a cooling rate calculated | required using the temperature of the steel plate surface.

The method for producing a wear-resistant steel plate of the present invention further includes any one of the following treatments (i) and (ii):
(I) The quenching is stopped at a quenching stop temperature equal to or lower than the Mf point, and then the quenched hot-rolled steel sheet is reheated to a tempering temperature.
(Ii) The quenching is stopped at the tempering temperature.
Hereinafter, each of the above (i) and (ii) will be described.

[Process (i)]
Quenching stop temperature: Mf point or less When the quenching stop temperature in the quenching step is higher than the Mf point, the volume ratio of martensite cannot be sufficiently increased, and the hardness of the steel sheet decreases. Therefore, the quenching is stopped at a quenching stop temperature equal to or lower than the Mf point. The quenching stop temperature is preferably 200 ° C. or lower, more preferably 150 ° C. or lower, and further preferably 120 ° C. or lower. On the other hand, the lower limit of the quenching stop temperature is not particularly limited, but excessive cooling causes a decrease in production efficiency, so the quenching stop temperature is preferably 20 ° C. or higher, and more preferably 30 ° C. or higher.

Reheating to tempering temperature After the quenching is stopped, the quenched hot-rolled steel sheet is reheated to the tempering temperature. By performing the reheating, the quenched steel sheet is tempered. As described above, when the tempering temperature is lower than (Mf point−100 ° C.), the dislocation density cannot be lowered, and therefore the bending workability is not improved. Therefore, the tempering temperature is set to (Mf point−100 ° C.) or higher. The tempering temperature is preferably (Mf point−90 ° C.) or higher, and more preferably (Mf point−80 ° C.) or higher. On the other hand, as described above, when the tempering temperature is higher than the Mf point, although the dislocation density is decreased, the surface hardness is significantly decreased. Therefore, the tempering temperature is set to the Mf point or less. The tempering temperature is preferably (Mf point−10 ° C.) or less, and more preferably (Mf point−20 ° C.) or less.

  The reheating can be performed by any method such as heating using a heat treatment furnace, high-frequency induction heating, or energization heating. The reheating can be performed either offline or online.

  Next, two preferred embodiments of the process (i) will be described.

・ Production conditions A
(When holding temperature after reheating)
In the said process (i), after re-heating the quenched hot-rolled steel plate to the said tempering temperature, the said re-heated hot-rolled steel plate can further be hold | maintained at the said tempering temperature. Hereinafter, this manufacturing condition is referred to as “manufacturing condition A”. Although the time (henceforth "holding time") hold | maintained at the said tempering temperature is not specifically limited, From a viewpoint of improving the effect of tempering, it is preferable to set it as 30 seconds or more, and it shall be 1 minute or more. More preferred. On the other hand, if the holding time is excessively long, the hardness of the steel sheet is lowered, so the holding time is preferably 60 minutes or less, more preferably 30 minutes or less, and even more preferably 20 minutes or less.

  When the temperature is maintained, the reheating is preferably performed using a heat treatment furnace. Moreover, in this manufacturing condition A, it is preferable that the average temperature increase rate at the time of the said reheating shall be 0.1-10 degrees C / s. In addition, after the holding time has elapsed, for example, furnace cooling or air cooling can be performed.

・ Production conditions B
(When performing rapid heating after quenching)
In the said process (i), reheating to the said tempering temperature can also be performed by rapid heating. In that case, it is preferable that the average temperature increase rate in the said reheating shall be 5 degrees C / s or more. By setting the average temperature rising rate to 5 ° C./s or more, carbides can be finely precipitated, and as a result, bending workability is improved. More preferably, the average heating rate is 10 ° C./s or more. Hereinafter, this manufacturing condition is referred to as “manufacturing condition B”. On the other hand, the upper limit of the average temperature increase rate is not particularly limited, but if the temperature increase rate is excessively increased, the equipment for performing reheating increases in size, and an increase in power consumption becomes a problem. Therefore, the average temperature rising rate is preferably 30 ° C./s or less, and more preferably 25 ° C./s or less.

  When the rapid heating is performed, the reheating may be stopped after reaching the tempering temperature. Although it does not specifically limit after stopping reheating, For example, the reheated hot-rolled steel plate can be air-cooled. In addition, as long as the effect of this invention is not impaired, after the said reheating, performing water cooling and performing both water cooling and air cooling is also accept | permitted.

  When the rapid heating is performed, the heating is preferably performed by high frequency induction heating or current heating. From the viewpoint of productivity, the rapid heating is preferably performed online, and the hot rolling, quenching, and rapid heating are more preferably performed on the same line.

・ Production conditions C
[Process (ii)]
In process (ii), after quenching, the quenched hot-rolled steel sheet is air-cooled. The quenching stop temperature in the quenching is set to the tempering temperature, that is, (Mf point−100 ° C.) or more and Mf point or less. Thereby, similarly to the case of the said process (i), a steel plate is tempered and a dislocation density can be reduced. Hereinafter, this manufacturing condition is referred to as “manufacturing condition C”.

Quenching stop temperature: (Mf point−100 ° C.) or more and Mf point or less If the quenching stop temperature in the quenching step is higher than the Mf point, the volume ratio of martensite cannot be sufficiently increased, and the hardness of the steel sheet decreases. . Therefore, the quenching is stopped at a quenching stop temperature equal to or lower than the Mf point. The quenching stop temperature is preferably (Mf point −10 ° C.) or less, and more preferably (Mf point −20 ° C.) or less. On the other hand, when the quenching stop temperature is lower than (Mf point−100 ° C.), the dislocation density cannot be lowered, and therefore the bending workability is not improved. Therefore, the quenching stop temperature is set to (Mf point−100 ° C.) or higher. The quenching stop temperature is preferably (Mf point−90 ° C.) or higher, and more preferably (Mf point−80 ° C.) or higher.

  Molten steel having the composition shown in Table 1 was melted to form a steel slab. Using the obtained steel slab, a wear-resistant steel plate was produced under each of the above production conditions A, B, and C. The specific manufacturing procedure was as follows.

・ Production conditions A
The following treatments (1) to (4) were sequentially performed on the steel slab:
(1) heating,
(2) hot rolling,
(3) Direct quenching or reheat quenching, and (4) Tempering.

  Table 2 shows the processing conditions in each step. The tempering was performed by reheating the quenched hot-rolled steel sheet to the tempering temperature shown in Table 2 using a heat treatment furnace, and then holding the tempering temperature for the holding time shown in Table 2. After the holding time, the tempered steel sheet was air-cooled. For comparison, tempering was not performed in some comparative examples.

・ Production conditions B
The following treatments (1) to (4) were sequentially performed on the steel slab:
(1) heating,
(2) hot rolling,
(3) Direct quenching or reheat quenching, and (4) Rapid heating.

  Table 3 shows the processing conditions in each step. The rapid heating was performed immediately after the quenching by using a high frequency induction heating device. The average heating rate and heating temperature in the rapid heating were as shown in Table 3. After the rapid heating, the heated steel sheet was air-cooled. For comparison, rapid heating was not performed in some comparative examples.

・ Production conditions C
The following treatments (1) to (4) were sequentially performed on the steel slab:
(1) heating,
(2) hot rolling,
(3) Direct quenching or reheat quenching, and (4) Air cooling.

  Table 4 shows the processing conditions in each step. In direct quenching or reheating quenching, cooling was stopped at the quenching stop temperature shown in Table 4. Further, after the quenching, the quenched steel plate was air-cooled.

  Next, the surface hardness, the volume ratio of martensite, the dislocation density, the density of inclusions / precipitates, and the critical bending radius were evaluated for each of the wear-resistant steel plates obtained under the above conditions. The evaluation method is as follows.

(surface hardness)
A specimen for hardness measurement was collected from the obtained wear-resistant steel plate, and the Brinell hardness was measured in accordance with the provisions of JIS Z 2243 (1998). The measurement was carried out after grinding and removing a region from the steel plate surface to a depth of 1 mm in order to eliminate the influence of the scale and decarburized layer present on the wear-resistant steel plate surface. Therefore, the measured hardness is the surface hardness in a plane having a depth of 1 mm from the steel sheet surface. In the measurement, a tungsten hard sphere having a diameter of 10 mm was used, and the load was 3000 kgf. The measurement position was the center in the width direction of the steel sheet.

(Volume ratio of martensite)
Samples were taken from each steel sheet so that the position at the center of the steel sheet in the width direction and the depth of 1 mm from the surface was the observation position. The surface of the sample was mirror-polished and further subjected to nital corrosion, and then a range of 10 mm × 10 mm was photographed using a scanning electron microscope (SEM). The imaged image was analyzed using an image analyzer to determine the martensite area fraction. Ten visual fields were observed at random, and the average value of the obtained area fractions was defined as the martensite volume fraction.

(Dislocation density)
A test piece for measuring dislocation density having a width of 25 mm and a length of 25 mm was taken from the obtained wear-resistant steel plate so that the measurement position was in the center in the width direction of the steel plate, and the dislocation density was measured. The measurement was performed after removing a region from the steel plate surface to a depth of 1 mm by grinding, mechanical polishing, and electrolytic polishing in order to remove the influence of the scale and the processed structure existing on the wear-resistant steel plate surface. Therefore, the measured dislocation density is a dislocation density in a plane having a depth of 1 mm from the steel sheet surface. The dislocation density was calculated by obtaining a line profile by X-ray diffraction measurement and analyzing the obtained line profile using the modified Williamson-Hall method and the modified Warren-Averbach method. The X-ray diffraction measurement was performed under the following conditions.
Voltage: 40 kV,
Current: 150 mA
X-ray source: CuKα

(Density of inclusions and precipitates)
Samples were taken from each steel sheet so that the position at the center of the steel sheet in the width direction and the depth of 1 mm from the surface was the observation position. The surface of the sample was mirror-polished, and an area of 10 mm × 10 mm was photographed using SEM. The particle size and number of inclusions / precipitates were determined by analyzing the photographed image using an image analyzer, the number of inclusions / precipitates having an average particle size of 500 nm or more was measured, and the density was determined. .

(Limit bending radius)
A bending test piece having a width of 50 mm and a length of 150 mm was collected from the obtained steel plate, and a bending test was performed at a bending angle of 180 ° in accordance with the provisions of JIS Z 2248. In the bending test, the critical bending radius R / t was determined from the minimum bending radius R (mm) at which no cracks occurred and the plate thickness t (mm). When the limit bending radius R / t was 2.8 or less, it was determined that the bending workability was good.

  The evaluation results obtained by the above method are also shown in Tables 2 to 4.

  As can be seen from the results shown in Tables 2 to 4, the wear-resistant steel plate that satisfies the conditions of the present invention had excellent wear resistance and bending workability. As described above, according to the present invention, the bending workability can be improved without reducing the surface hardness of the wear-resistant steel sheet, which is extremely useful industrially.

Claims (13)

% By mass
C: more than 0.23%, 0.34% or less,
Si: 0.05-1.00%,
Mn: 0.05-2.00%
P: 0.020% or less,
S: 0.050% or less,
Al: 0.100% or less,
Cr: 0.05-0.90%
N: 0.0050% or less, and O: 0.0050% or less,
It has a component composition consisting of the balance Fe and inevitable impurities,
The hardness at a depth of 1 mm from the surface is 460-590 HBW 10/3000 in terms of Brinell hardness,
The volume ratio of martensite at a depth of 1 mm from the surface is 90% or more,
Dislocation density ρ (m ⁻² ) at a depth of 1 mm from the surface, and ρ _u defined by the following equation (2) using the Mf point defined by the following equation (1), the following equation (3) Satisfied, wear-resistant steel plate.
Mf (° C.) = 410.5−407.3 × C−7.3 × Si-37.8 × Mn−20.5 × Cu−19.5 × Ni−19.8 × Cr−4.5 × Mo ... (1)
ρ _u (m ⁻² ) = 15 × 10 ¹⁵ × C + 2 × 10 ¹⁵ −5.74 × 10 ⁹ × (Mf−100) ² −1.05 × 10 ¹¹ × (Mf−100) (2)
ρ ≦ ρ _u (3)
(However, the element symbols in the above formulas (1) and (2) are the contents of each element expressed in mass%, and the contents of the elements not contained are 0) The component composition is mass%,
Nb: 0.005 to 0.025%,
Ti: 0.005-0.030%, and B: 0.0001-0.0018%
The wear-resistant steel sheet according to claim 1, further comprising one or more selected from the group consisting of: The component composition is mass%,
Cu: 0.01 to 1.00%,
Ni: 0.01 to 5.00%,
Mo: 0.01-2.00%,
V: 0.01 to 1.00%,
W: 0.01-1.00%, and Co: 0.01-1.00%
The wear-resistant steel plate according to claim 1 or 2, further comprising one or more selected from the group consisting of: The component composition is mass%,
Ca: 0.0005 to 0.0100%,
Mg: 0.0005 to 0.0100%, and REM: 0.0005 to 0.0100%
The wear-resistant steel sheet according to any one of claims 1 to 3, further comprising one or more selected from the group consisting of: The wear-resistant steel sheet according to any one of claims 1 to 4, wherein the density of inclusions and precipitates having an average particle diameter of 500 nm or more at a depth of 1 mm from the surface is 3.0 pieces / mm ² or less. % By mass
C: more than 0.23%, 0.34% or less,
Si: 0.05-1.00%,
Mn: 0.05-2.00%
P: 0.020% or less,
S: 0.050% or less,
Al: 0.100% or less,
Cr: 0.05-0.90%
N: 0.0050% or less, and O: 0.0050% or less,
A steel material having a component composition consisting of the remaining Fe and inevitable impurities is heated to a heating temperature,
Hot-rolling the heated steel material into a hot-rolled steel sheet,
Quenching the hot-rolled steel sheet starts from a quenching start temperature,
The quenching is stopped at a quenching stop temperature equal to or lower than the Mf point defined by the following formula (1), and then the quenched hot-rolled steel sheet is reheated to a tempering temperature, or
Stopping the quenching at the tempering temperature, then air-cooling the quenched hot-rolled steel sheet,
The quenching is direct quenching in which the quenching start temperature is not lower than the Ar ₃ transformation point, or reheating quenching in which the quenching start temperature is not lower than the Ac ₃ transformation point,
The method for producing a wear-resistant steel sheet, wherein the tempering temperature is (Mf point−100 ° C.) or more and Mf point or less.
Mf (° C.) = 410.5-407.3 × C-7.3 × Si-37.8 × Mn-20.5 × Cu-19.5 × Ni-19.8 × Cr-4.5 × Mo ... (1)
(However, the element symbol in the above formula (1) is the content of each element expressed in mass%, and the content of the element not contained is 0) The component composition is mass%,
Nb: 0.005 to 0.025%,
Ti: 0.005-0.030%, and B: 0.0001-0.0018%
The method for producing a wear-resistant steel sheet according to claim 6, further comprising one or more selected from the group consisting of: The component composition is mass%,
Cu: 0.01 to 1.00%,
Ni: 0.01 to 5.00%,
Mo: 0.01-2.00%,
V: 0.01 to 1.00%,
W: 0.01-1.00%, and Co: 0.01-1.00%
The method for producing a wear-resistant steel plate according to claim 6 or 7, further comprising one or more selected from the group consisting of: The component composition is mass%,
Ca: 0.0005 to 0.0100%,
Mg: 0.0005 to 0.0100%, and REM: 0.0005 to 0.0100%
The manufacturing method of the abrasion-resistant steel plate as described in any one of Claims 6-8 which further contains 1 or 2 or more selected from the group which consists of. The density of inclusions and precipitates having an average particle diameter of 500 nm or more at a depth of 1 mm from the surface of the wear-resistant steel sheet is 3.0 pieces / mm ² or less, according to any one of claims 6 to 9. Method for producing a wear-resistant steel sheet. It is a manufacturing method of the wear-resistant steel plate according to any one of claims 6 to 10,
The quenching is stopped at a quenching stop temperature below the Mf point,
Then, the quenched hot rolled steel sheet is reheated to the tempering temperature,
Furthermore, the manufacturing method of the abrasion-resistant steel plate which hold | maintains the said reheated hot-rolled steel plate at the said tempering temperature. It is a manufacturing method of the wear-resistant steel plate according to any one of claims 6 to 10,
The quenching is stopped at a quenching stop temperature below the Mf point,
Next, the method for producing a wear-resistant steel sheet, wherein the quenched hot-rolled steel sheet is reheated to the tempering temperature at an average temperature increase rate of 5 ° C./s or more. It is a manufacturing method of the wear-resistant steel plate according to any one of claims 6 to 10,
Stop the quenching at the tempering temperature,
Next, a method for producing a wear-resistant steel sheet, wherein the quenched hot-rolled steel sheet is air-cooled.

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