JPH108186A - Wear resistant steel plate excellent in bendability - Google Patents

Abstract

PROBLEM TO BE SOLVED: To produce an inexpensive wear resistant steel plate, particularly wear resistant steel plate for welding, excellent in bendability and capable of preventing stress concentration. SOLUTION: The surface layer part of this steel plate is composed of martensitic structure or mixed structure of martensite and bainite. Moreover, the Vickers hardness of the surface layer part of the steel plate is regulated to 300-550, and further, the relationship among the Vickers hardness HVs in the boundary position between the surface layer and the inner part of the steel plate, the Vickers hardness HVc in the central position in the inner part of the steel plate, and the plate thickness (t) (mm) of the steel plate satisfies (HVs-HVs)>=0.4×t when the plate thickness (t) of the steel plate is <30mm and also satisfies (HVs-HVc)>=(0.6×t-6) when the plate thickness (t) of the steel plate is >=30mm, respectively.

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a wear-resistant steel plate having excellent bending workability, and more particularly to a welding wear-resistant steel plate having excellent bending workability. This steel plate
It can be used for all structural members requiring bending workability, wear resistance and weldability, such as industrial machines, mining-related devices, and building-related devices.

[0002]

2. Description of the Related Art After abrasion-resistant steel sheets are cut into predetermined shapes,
It performs bending and welding, and is used for structural members such as industrial machines, mining-related devices, and building-related devices. These structural members are often used as they are bent or after welding. In order to improve the life, wear-resistant steel sheets having high surface hardness are required. As means for increasing the surface hardness of the wear-resistant steel plate, a large amount of alloying elements such as C have been added to improve the hardenability (Japanese Patent Laid-Open Nos. 5-214485 and 5-239590). reference). However, when a large amount of alloying elements is added, the hardness of the wear-resistant steel plate can be increased, but there has been a problem that processing cracks occur during processing such as cutting, bending, and welding. In particular, the bending workability was significantly deteriorated, and the weldability was also a serious problem.

In order to solve such problems, there has been proposed a composite steel sheet in which the surface layer is made of a high-hardness steel and the inside is laminated with steel having a lower hardness than the surface layer (Japanese Patent Laid-Open No. 22223/1991).
3 publication). This composite steel sheet has a structure in which the surface layer portion has a high hardness to enhance wear resistance, and the inside has a low hardness to ensure workability and weldability.

[0004]

However, in the production of the above-mentioned composite steel sheet, since the surface layer and the inside are composited by continuous casting, the equipment and the production method become complicated, and the production cost increases. In addition, cracks may occur at the interface between the composite surface layer and the interior during bending due to the composite material.
When appropriate bending workability is required, there is a limit in increasing the hardness of the surface layer portion, and it is conceivable that improvement in wear resistance cannot be expected. Further, since the difference in hardness at the interface between the composite surface layer portion and the inside increases, stress concentration is likely to occur, and the fatigue strength may be reduced to shorten the life of the structural member.

Accordingly, an object of the present invention is to provide a wear-resistant steel plate which is inexpensive, has excellent bending workability and can prevent stress concentration, particularly a wear-resistant steel plate for welding.

[0006]

In order to achieve the above-mentioned object, a wear-resistant steel plate which can prevent cracking during bending, suppress stress concentration and have excellent weldability without impairing wear resistance. Research and development. The inventors have conducted intensive studies on the thickness, structure, chemical composition, and heat treatment method of the wear-resistant steel plate and completed the present invention.

[0007] In the present invention, the surface layer of the steel sheet has a martensite structure or a mixed structure of martensite and bainite, and the Vickers hardness of the surface layer of the steel sheet is in the range of 300 to 550. The relationship between the Vickers hardness HVs at the boundary between the surface layer and the inside of the steel sheet, the Vickers hardness HVc at the center position inside the steel sheet, and the thickness t (mm) of the steel sheet is represented by the thickness t of the steel sheet.
Is less than 30 mm, HVs−HVc ≧ 0.4 × t... (1), and when the thickness t of the steel sheet is 30 mm or more, HVs−HVc ≧ 0.6 × t−6. (2) It is characterized by the following.

According to the present invention, (a) the surface layer of the steel sheet has a martensite structure or a mixed structure of martensite and bainite, and the surface layer has a Vickers hardness of 300 to 300.
By setting it in the range of 550, excellent wear resistance can be obtained. Next, (b) the relationship between the Vickers hardness at the boundary position between the surface layer portion and the inside and the Vickers hardness at the center position inside the steel plate and the plate thickness satisfies the expression (1) or the expression (2). It can have bending workability. Further, (c) since the entire steel sheet has a uniform component, stress concentration can be suppressed.

The higher the Vickers hardness of the surface layer of a wear-resistant steel plate, the higher the wear resistance. The wear-resistant steel plate of the present invention has a further improved wear resistance by setting the Vickers hardness to 300 or more. On the other hand, if the Vickers hardness of the surface layer exceeds 550, the bending workability is significantly reduced. In addition, it is said that the Vickers hardness of 200 or more is sufficient for abrasion resistance for normal use.

Next, the results of a study on the bending workability of a wear-resistant steel plate will be described. Abrasion-resistant steel plates having various chemical components having a thickness t of 9 to 55 mm were heat-treated, and the surface layer was made to have a martensite structure or a mixed structure of martensite and bainite. At this time, the Vickers hardness of the surface layer portion of the wear-resistant steel plate was in the range of 300 to 550, and the Vickers hardness of the central portion was lower than the Vickers hardness of the surface layer portion. A wide bending test was performed on these wear-resistant steel plates. The result is shown in FIG. The horizontal axis represents the thickness t of the wear-resistant steel sheet, and the vertical axis represents the Vickers hardness HVs at the boundary between the surface layer and the inside of the steel sheet and the Vickers hardness HV at the center position inside the steel sheet.
Difference of c: HVs-HVc is shown. In the wide bending test, the boundary position between the surface layer and the inside of the wear-resistant steel plate was set to a position 2 mm from the surface of the wear-resistant steel plate. Usually, since the surface of the steel sheet is softened by decarburization, a position 2 mm from the surface not affected by decarburization plays a large role in abrasion resistance. For this reason, it is preferable that the boundary position between the surface layer portion and the center portion of the steel sheet is set to 2 mm from the surface of the steel sheet. This position is composed of a martensite structure or a mixed structure of martensite and bainite and has a Vickers hardness of 3
It is preferably in the range of 00 to 550.

As shown in FIG. 1, it has been found that the wear-resistant steel sheet of the present invention has a region in which bending cracking does not occur even if the surface layer has a Vickers hardness of 300 to 550. The region above the solid line bending crack generation limit curve is a region where cracking due to bending does not occur. The abrasion-resistant steel sheet of the present invention is manufactured by using the Vickers hardness (200 to 26) of the surface layer portion of the composite steel sheet in the example of JP-A-3-227233.
0) It was found that bending cracking did not occur in the region of higher hardness. The wear-resistant steel plate of the present invention has a uniform composition,
It is considered that the bending also could be prevented by continuously changing the hardness.

The bending crack generation limit curve is represented by a sheet thickness t.
Is larger, the difference between the Vickers hardness at the boundary position between the surface layer portion and the inside of the steel sheet and the Vickers hardness at the center position “HVs
−HVc ”has increased. That is, it is clear that Vickers hardness inside the surface layer of the wear-resistant steel plate must be lower than that of the surface layer. When the thickness t of the steel sheet is less than 30 mm, HVs−HVc = 0.4 × t (1) On the other hand, when the thickness t of the steel sheet is 30 mm or more, HVs−HVc = 0.6 × t−6... (2)

The wear-resistant steel plate of the present invention preferably has a thickness of 9 mm or more. If the plate thickness is less than 9 mm, the influence of the hardness of the surface layer portion becomes large, and does not contribute to the improvement of the bending workability. The upper limit of the plate thickness is the range of a commonly used thick plate: 12
Although it is applicable up to 0 mm, a plate thickness of 90 mm or less is preferable. The width of the plate is not particularly limited, and the width of a generally used wear-resistant steel plate is 4500 mm or less. When used for members such as industrial machines, mining-related devices, and building-related devices, this wear-resistant steel plate is cut into a predetermined shape and bent. The wear-resistant steel plate of the present invention has a thickness and a width corresponding thereto.

The invention according to claim 2 is characterized in that:
C: 0.04 to 0.30%, Si: 0.05 to 2.0
%, Mn: 0.50 to 3.0%, Zr: 0.005 to
0.20%, N: 0.0020 to 0.020%, the balance being Fe and a wear-resistant steel plate which is an unavoidable impurity element. This wear-resistant steel plate has wear resistance and improves bending workability and weldability. In particular, Zr
By adding, carbides in the wear-resistant steel can be finely dispersed in a spherical shape to improve bending workability. Also, by adding Zr and N in combination, the maximum hardness of the weld heat affected zone is lowered,
The toughness of the weld can be improved.

According to the third aspect of the invention, wear resistance and tensile strength can be increased by adding 0.04 to 2.0% of Cr to the second aspect of the invention. Further, the strength of the weld can be increased.

The reasons for limiting the component range of the wear-resistant steel sheet having excellent bending workability according to the present invention will be described below. (A) C: 0.04 to 0.30% C is an element necessary for hardening steel, improving wear resistance and tensile strength, and these effects can be obtained when the amount of C is less than 0.04%. Absent. On the other hand, if the C content exceeds 0.30%, the weldability is significantly reduced.

(B) Si: 0.05 to 2.0% Si is necessary for deoxidizing molten steel and is an element necessary for improving tensile strength. In order to ensure the deoxidizing effect of molten steel, it is necessary to add Si in an amount of 0.05% or more. Also,
If the Si content exceeds 2.0%, the hot rolling property and the weldability are reduced, and the toughness of the weld is further deteriorated.

(C) Mn: 0.5 to 3.0% Mn is necessary for deoxidizing molten steel and is an element necessary for improving wear resistance and tensile strength. If the Mn content is less than 0.5%, these effects cannot be obtained. If the Mn content exceeds 3.0%, the weldability will decrease.

(D) Zr: 0.005 to 0.20% Zr is an element which disperses carbides in steel into fine particles in a spherical shape, and is effective for improving bending workability and preventing delayed fracture. Further, the generated Zr nitride becomes a precipitation nucleus of ferrite at the time of welding, promotes precipitation of ferrite, can reduce the maximum hardness of the weld heat affected zone, and contributes to improvement of toughness of the weld zone. . To obtain these effects, Zr is set to 0.0
It is necessary to add at least 05%. If the Zr content exceeds 0.2%, the toughness of the steel and the weld heat affected zone deteriorates.

(E) N: 0.002 to 0.020% N must be added in an amount of 0.002% or more in order to form a Zr nitride having an effect of lowering the maximum hardness of the weld heat affected zone. There is. If the N content exceeds 0.020%, the toughness of the steel and the weld heat affected zone deteriorates.

(F) Cr: 0.04 to 2.0% Cr is an element effective for improving the wear resistance and increasing the tensile strength. Further, the strength of the weld can be increased. By adding 0.04% or more of Cr, wear resistance and tensile strength are improved. Cr content is 2.0%
If it exceeds, the weldability and toughness are significantly reduced.

(G) P, S: not more than 0.02% Since P and S embrittle the grain boundaries of steel, both of them are 0.0% or less.
It is preferable that the content be 2% or less.

Next, the results of a study on heat treatment of a wear-resistant steel plate will be described. The heat treatment of the abrasion-resistant steel sheet is usually performed by holding the material at a temperature of not less than the A _C3 transformation point in a heating furnace and then cooling the material to 450 ° C. or less by quenching. Thereafter, if necessary, tempering is performed at a temperature lower than the A _C1 transformation point. As a result, the surface layer of the wear-resistant steel plate has a martensite structure or a mixed structure of martensite and bainite. The Vickers hardness of the surface layer of the wear-resistant steel plate can be in the range of 300 to 550.

The relationship between the Vickers hardness HVs at the boundary between the surface layer portion and the inside of the wear-resistant steel plate, the Vickers hardness HVc at the center position inside the steel plate, and the plate thickness t (mm) of the steel plate is expressed by the above equation (1). Or, a heat treatment method and an alloy composition satisfying the expression (2) were examined. As a result, an alloy composition of a wear-resistant steel plate that satisfies the above expression (1) or (2) under the above heat treatment conditions was found. That is, in the wear-resistant steel sheet, the relation between the carbon equivalent Ceq (mass%) and the thickness t (mm) of the steel sheet satisfies Ceq ≦ 0.008 × t + 0.25 (3) It is. When the sheet thickness t of the steel sheet is 25 mm or less, it is preferable that the steel sheet satisfy the following condition: Ceq ≦ 0.014 × t + 0.1 (4). Here, carbon equivalent Ceq =
C + Mn / 6 + (Cr + Mo + V) / 5 + (Cu + N
i) / 15. This equation of carbon equivalent Ceq is adopted by the International Welding Society (IIW).

Further, the process of deriving this relationship will be described.
I do. The wear-resistant steel sheet shown in Table 1 was hardened and hardened as shown in Table 2.
Heat treatment was performed under the return condition. Of these, A_C3transformation
After holding above the point, cooling to 450 ° C or less by quenching
And A in the heating furnace _C3After holding above the transformation point, bake
After cooling to a temperature of 450 ° C. or less_C1Below the transformation point
Sheet thickness t of the steel sheet tempered at
Fig. 2 is a plot of the relationship between
Was. These steel sheets were subjected to a wide bending test. Figure
2 is the steel sheet of the present invention, and the bending crack was generated.
That was not. On the other hand, △ indicates occurrence of bending crack
It was done. Generally, high wear resistance with high carbon equivalent Ceq
Cracking has occurred in the steel plate. That is, good hardenability
A good steel plate is cracked.

Next, regarding the steel sheet, the horizontal axis represents the thickness t of the steel sheet, and the vertical axis represents the difference between the Vickers hardness HVs at a position 2 mm from the surface of the steel sheet and the Vickers hardness HVc at a central position inside the steel sheet. FIG. 3 in relation to “HVs−HVc”
Are plotted. As shown in FIG. 3, the wear-resistant steel plate of the present invention marked by “○” is located above the same bending crack initiation limit curve as shown in FIG. 1. That is, the relationship between the Vickers hardness HVs at the boundary position between the surface layer portion and the inside of the steel sheet, the Vickers hardness HVc at the center position inside the steel sheet, and the plate thickness t (mm) of the steel sheet is expressed by equation (1) or (2). It satisfies the formula. Carbon equivalent Ce of the wear-resistant steel sheet of the present invention
Since q is low, the hardenability into the inside of the steel sheet is deteriorated, and the increase in hardness inside is small, and therefore, 2 mm from the surface of the steel sheet.
The difference "HVs-HVc" between the Vickers hardness HVs at the position V and the Vickers hardness HVc at the center position inside the steel plate increases.

[0027]

[Table 1]

[0028]

[Table 2]

In FIG. 17 and Experiment N
o. The steel sheet No. 18 has a carbon equivalent Ceq (% by mass) and a sheet thickness t.
Although the relationship with (mm) satisfied the expression (3), bending cracking occurred. This will be described. In these steel sheets, B is added to refine the precipitate. B is usually 0.001% and is an element which remarkably improves hardenability. Experiment No. 17 and Experiment No. 1
In the steel sheet No. 8, B was 0.0012% and 0.001, respectively.
Contains 4%. Therefore, in Experiment No. 17 and Experiment N
o. The steel plate No. 18 is “HVs-HVc” as shown in FIG.
Is smaller, and the expression (1) or (2) is no longer satisfied.

The carbon equivalent Ceq (% by mass) and the plate thickness t (m
m) satisfies the expression (3) or the expression (4),
The wear-resistant steel sheet to which B is not added is kept in a heating furnace at a temperature not lower than the A _C3 transformation point, and then cooled to a temperature of 450 ° C. or lower by quenching. Thereafter, if necessary, tempering is performed at a temperature lower than the A _C1 transformation point. The wear-resistant steel sheets subjected to these heat treatments have a Vickers hardness HVs at the boundary between the surface layer and the inside of the steel sheet and a Vickers hardness HV at the center position inside the steel sheet.
The relationship between c and the thickness t (mm) of the steel sheet satisfies the expression (1) or (2).

The Vickers hardness at the center of the wear-resistant steel plate
Lowering the hardness than the surface layer and Vickers hardness is another
Heat treatment is possible. That is, induction hardening, flame quenching
It can be achieved by performing surface quenching such as putting. This
The heating temperature of the surface layer is A _C3Above the transformation point. necessary
A according to_C1Tempering is performed at a temperature below the transformation point.

[0032]

DESCRIPTION OF THE PREFERRED EMBODIMENTS An embodiment of the present invention will be described. Table 1
Abrasion resistant steels having the chemical components shown in Table 2 were melted, rolled, and heat-treated to produce test materials shown in Table 2. A test material was sampled from the test material and subjected to a hardness test, a microstructure observation, a tensile test, and a wide bending test. The results are shown in Table 2. The steel numbers A to I in Table 1 are the steels of the present invention, and the steel numbers J to O are comparative steels. Also, in Experiment 2 of Table 2, The steel sheets of Nos. 1 to 9 are the materials of the present invention, and Steel plates 11 to 18 are comparative materials.

The hardness test was performed with a Vickers hardness tester and a load of 30.
kgf. The microstructure was observed by polishing the test material and then observing the microstructure at a position 2 mm from the surface of the steel sheet.
The tensile test was performed using a tensile test piece according to JIS Z 22011. Wide bending test: thickness x 500 x 500m
The test was performed using a wide bending test piece of m. The wide bending test
With a metal fitting with a tip radius of 5 mm, V of JIS Z 2248
A block method bending test was performed to evaluate the occurrence of cracks at a bending angle of 90 °.

Experiment No. of the material of the present invention Steel plates 1 to 9 are
As shown in Table 2, the Vickers hardness was 300 or more, and the surface layer (at a position 2 mm from the surface) was composed of a martensite structure or a mixed structure of martensite and bainite. As a result, it has excellent wear resistance. It has a high tensile strength of 980 N / mm ² or more. Usually, the higher the tensile strength, the higher the fatigue strength. Further, since the tensile strength increases as the Vickers hardness increases, the wear-resistant steel plate of the present invention has excellent fatigue strength. Further, the hardness and the microstructure were continuously changed from the surface layer portion to the central portion, and there was no discontinuous portion. As a result, stress concentration hardly occurs and fatigue strength is high, so that the life of structural members can be expected to be improved.

Experiment No. of the material of the present invention. Steel plates 1 to 9 are
In the evaluation of 90 ° bending by the wide bending test, no crack was generated. In the steel sheet of the material of the present invention, the relationship between the Vickers hardness HVs at the boundary position (2 mm from the surface part) and the Vickers hardness HVc at the center position and the thickness t (mm) of the surface layer and the inside is expressed by the above formula (1) or It was confirmed from the hardness test that the formula (2) was satisfied. Further, the experiment Nos. The steel sheets 1 to 9 did not have any problem in the weldability. The material of the present invention can be used for structural members such as industrial machines, mining-related devices, and building-related devices.

Next, the relationship between the material of the present invention and the comparative material will be described. Some are described above in the section of the solution to the problem. Experiment No. Nos. 1 and 11 and Experiment Nos. 2 and 13 are the same as steel number A and steel number, respectively. Experiment No. Nos. 1 and 2 have high Vickers hardness and do not cause bending cracks. On the other hand, in Experiment No. Samples Nos. 11 and 13 had low Vickers hardness and caused bending cracks. Experiment No. Nos. 1 and 2 satisfy the above equation (1) or (2) and have high Vickers hardness by appropriate heat treatment. Along with this, the tensile strength is increased, and the wear-resistant steel plate is excellent in wear resistance and tensile strength. Note that the experiment No. Thirteen of the surface layer portions and the inner boundary position (2 mm from the surface portion) were composed of a mixed structure of ferrite and bainite.

Experiment No. The steel sheets Nos. 16, 17 and 18 were prepared by adding B to refine the precipitates and improve the hardenability. These steel sheets had high Vickers hardness and tensile strength, but had bending cracks. In these steel plates, the relationship between the Vickers hardness of 2 mm from the surface, the Vickers hardness at the center position, and the plate thickness does not satisfy the above formula (1) or (2). This is because the hardenability was remarkably improved by the addition of B. Therefore, it is preferable that B is not added to the wear-resistant steel sheet of the present invention. Experiment No. Bending cracks also occurred in steel sheets 12, 14, and 15. Similarly, in these steel plates, the relationship between the Vickers hardness of 2 mm from the surface, the Vickers hardness at the center position, and the plate thickness did not satisfy the above formula (1) or (2).

[0038]

As described above, the wear-resistant steel plate of the present invention is easy to manufacture and therefore inexpensive. This wear-resistant steel plate has a uniform component as a whole, and has a higher Vickers hardness than the conventional one by optimizing the relationship between the Vickers hardness at the boundary position between the surface layer and the inside and the Vickers hardness and the plate thickness at the center position inside the steel plate. Due to its hardness, it can have excellent bending workability. Due to high Vickers hardness, it has high tensile strength and excellent fatigue strength. In addition, there is no discontinuous portion from the surface layer to the center, and as a result,
Since stress concentration hardly occurs and fatigue strength is high, improvement in the life of structural members can be expected. Further, by adding Zr and N in a combined manner, the maximum hardness of the weld heat affected zone can be reduced, and the toughness of the weld zone can be improved.

As a result, it is possible to provide a wear-resistant steel plate which is inexpensive, has excellent bending workability and can prevent stress concentration, particularly a wear-resistant steel plate for welding. Further, the knowledge of the wear-resistant steel plate of the present invention can be applied to wear-resistant steel and the like.

[Brief description of the drawings]

FIG. 1 is a diagram showing the results of a wide bending test of an example of the present invention.

FIG. 2 is a diagram showing the results of a wide bending test of another example of the present invention.

FIG. 3 is a diagram showing the relationship between the plate thickness and the carbon equivalent of another embodiment of the present invention.

[Explanation of symbols]

t Vickers hardness at the boundary between the surface layer and the inside of the steel plate HVs Vickers hardness at the center position inside the HVc steel plate Ceq Carbon equivalent

Claims (5)

[Claims] 1. The steel sheet has a surface layer comprising a martensite structure or a mixed structure of martensite and bainite, the Vickers hardness of the surface layer portion of the steel sheet is in the range of 300 to 550, and the surface layer portion of the steel sheet is The relationship between the Vickers hardness HVs at the boundary position, the Vickers hardness HVc at the center position inside the steel plate and the plate thickness t (mm) of the steel plate is as follows: When the plate thickness t of the steel plate is less than 30 mm, HVs−HVc ≧ 0 0.4 × t, and when the thickness t of the steel sheet is 30 mm or more, HVs−HVc ≧ 0.6 × t−6. A wear-resistant steel sheet having excellent bending workability. 2. C: 0.04 to 0.30% by mass%
Si: 0.05 to 2.0%, Mn: 0.50 to 3.0
%, Zr: 0.005 to 0.20%, N: 0.002
0.020%, the balance being Fe and an unavoidable impurity element, wherein the surface layer portion of the steel sheet has a martensite structure or a mixed structure of martensite and bainite, and the surface layer portion of the steel sheet has Vickers hardness. In the range of 300 to 550, and the relationship between the Vickers hardness HVs at the boundary between the surface layer portion and the inside of the steel sheet, the Vickers hardness HVc at the center position inside the steel sheet, and the thickness t (mm) of the steel sheet, When the thickness t of the steel plate is less than 30 mm, HVs−HVc ≧ 0.4 × t, and when the thickness t of the steel plate is 30 mm or more, HVs−HVc ≧ 0.6 × t−6. Wear-resistant steel plate with excellent bending workability. 3. C: 0.04 to 0.30% by mass%,
Si: 0.05 to 2.0%, Mn: 0.50 to 3.0
%, Zr: 0.005 to 0.20%, N: 0.002
0.020%, Cr: 0.04 to 2.0%, the balance being Fe and an unavoidable impurity element, wherein the steel sheet has a martensite structure or a mixed structure of martensite and bainite. The surface layer portion Vickers hardness of the steel sheet is in the range of 300 to 550, and the Vickers hardness HVs at the boundary between the surface layer portion and the inside of the steel sheet, the Vickers hardness HVc at the center position inside the steel sheet, and the steel sheet. When the thickness t of the steel plate is less than 30 mm, HVs−HVc ≧ 0.4 × t, and when the thickness t of the steel plate is 30 mm or more, HVs−HVc ≧ 0. 6. A wear-resistant steel sheet having excellent bending workability, characterized in that it is 6 × t-6. 4. The wear-resistant steel sheet having excellent bending workability according to claim 1, wherein a boundary position between the surface layer portion and the inside of the steel sheet is 2 mm from the surface of the steel sheet. 5. A wear-resistant steel sheet excellent in bending workability according to claim 1, further comprising a carbon equivalent Ceq (mass%), a sheet thickness t (mm), and a thickness t (mm) of the wear-resistant steel sheet. Is a wear-resistant steel sheet excellent in bending workability, where Ceq ≦ 0.008 × t + 0.25. Here, carbon equivalent Ceq = C + Mn / 6 + (Cr + Mo
+ V) / 5 + (Cu + Ni) / 15.