JPWO2009087990A1 - Abrasion-resistant steel plate excellent in high-temperature wear resistance and bending workability and manufacturing method thereof - Google Patents

Abstract

This wear-resistant steel sheet is, by mass, C: 0.13% or more, 0.18% or less, Si: 0.5% or more, less than 1.0%, Mn: 0.2% or more, 0.8% Hereinafter, P: 0.020% or less, S: 0.010% or less, Cr: 0.5% or more, 2.0% or less, Mo: 0.03% or more, 0.30% or less, Nb: 0.0. More than 03%, 0.10% or less, Al: 0.01% or more, 0.20% or less, B: 0.0005% or more, 0.0030% or less, and N: 0.010% or less, The balance contains Fe and inevitable impurities, the component composition satisfies that HI is 0.7 or more and Ceq is more than 0.50, and HB (Brinell hardness) is 360 or more at 25 ° C., 440 It is as follows.

Description

The present invention relates to a wear-resistant steel plate excellent in high-temperature wear resistance and bending workability used for construction machinery and industrial machinery, and a method for producing the same.
This application claims priority to Japanese Patent Application No. 2008-000301 filed on January 7, 2008 and Japanese Patent Application No. 2008-268253 filed on October 17, 2008, The contents are incorporated here.

  Many construction machines for excavation and civil engineering work in mines require frequent replacement due to wear. Among them, a severe condition for steel is when it is used in a high temperature environment. As the temperature rises, the wear-resistant steel decreases in hardness, so the wear rate increases rapidly above a certain temperature. The wear is particularly noticeable in bulldozer buckets where frictional heat is generated by strong impacts, and sintered coke hoppers where high-temperature objects collide. It is supposed to be about 300 ° C to 400 ° C. Since frequent member replacement causes a reduction in equipment operation rate, a steel material having high wear resistance (abrasion resistant steel) is required even in such an environment.

  On the other hand, in order to apply to various shapes of parts, or to reduce the number of welds as much as possible, bending workability of steel sheets is often regarded as important for wear-resistant steel.

  Increasing the hardness is effective for improving the wear resistance. However, a steel sheet having a high hardness is likely to break or crack when it is bent with a small bending radius. Furthermore, considering the magnitude of deformation resistance to bending and springback, the high hardness of the steel sheet is disadvantageous for bending. That is, wear resistance and bending workability are generally contradictory characteristics. For example, wear resistant steel of the HB500 class (with a Brinell hardness of about 450 to 550 at room temperature) is excellent in wear resistance but not very good in bending workability. The wear resistant steel of the HB400 class (with a Brinell hardness of about 360 to 440 at room temperature) having a lower hardness can be bent relatively easily, and is applied to many members that require processing. Abrasion resistance, particularly in high temperature environments, is not sufficient.

  Therefore, in order to achieve both bending workability and high-temperature wear resistance, it can be said that it is an effective method to provide high-temperature wear resistance to wear-resistant steel having a normal temperature hardness of HB400 class.

  In general, steel sheets for wear-resistant applications do not require a particularly high toughness value, but a certain toughness value is set so that cracks do not occur even if the thickness of the steel sheet decreases during use. It is necessary to have. Considering use in cold regions, it is considered that Charpy absorbed energy at −40 ° C. is 27 J or more.

  The present inventors previously disclosed Patent Document 1 as a wear-resistant steel for high-temperature applications having a Brinell hardness HB500 class. The invention described in this document is designed with the highest priority on high temperature wear resistance, and does not take any special measures to improve the bending workability, and is therefore limited to applications where the bending radius is relatively gentle. .

  Patent document 2 relates to a wear resistant steel for medium room temperature used in a region where the temperature is changed from 300 ° C to 400 ° C. Here, toughness and workability are not taken into consideration and their characteristics are not shown, but because Si is very high, toughness is not high and workability is not high.

  Patent Document 3 relates to HB400 class wear-resistant steel having excellent bending workability, but no consideration is given to wear resistance in a high-temperature environment.

As described above, the HB400 class wear-resistant steel having good bending workability and the wear-resistant steel plate having high wear resistance even in a high temperature environment from 300 ° C. to 400 ° C. are suitable so far. I can't find it.
In addition, since the wear-resistant steel plate is a consumable item, economic efficiency is also an important factor, and it is desirable that the amount of expensive alloy elements added be as low as possible.
JP 2001-49387 A JP-A-3-243743 JP-A-2005-240135

  The present invention is a wear-resistant steel that is HB400 class room temperature hardness with good bending workability and has high wear resistance even in a high temperature environment of 300 ° C. to 400 ° C., and is also excellent in economy. The purpose is to provide.

  In order to improve the wear resistance at a high temperature from 300 ° C. to 400 ° C., it is considered important to maintain the hardness at this temperature as high as possible. On the other hand, the most economical means of obtaining room temperature hardness of about HB400 is to make the structure martensite. However, a martensitic steel sheet has a large decrease in hardness due to temperature rise. Then, about the steel (martensitic structure steel) containing the martensite structure | tissue which has a normal temperature hardness of about HB400, examination which improves high temperature abrasion resistance from a viewpoint of maintaining high temperature hardness as much as possible was performed.

  The present invention assumes a high temperature environment of 300 ° C. to 400 ° C., but the typical temperature for characteristic evaluation is set to 350 ° C., and the martensitic steel having various chemical compositions at 350 ° C. The wear resistance was investigated. The abrasion resistance evaluation was performed as follows. In a pin-on-disk type wear test device compliant with ASTM G99-05, the sample temperature is controlled so that the sample temperature is 350 ° C., and the wear amount of the test sample and the standard sample (SS400) is determined. It was measured. Then, using SS400 as a standard sample, [wear amount of SS400 / wear amount of test sample] was defined as a 350 ° C. wear resistance ratio, and this 350 ° C. wear resistance ratio was determined. It can be said that the larger this value, the better the wear resistance at 350 ° C.

  FIG. 1 shows 0.15% C-0.57% Si-0.41% Mn-1.37% Cr-0.08% Mo-0.012% Ti-0.0011% B-0.0032% This is the relationship between the Nb addition amount and the 350 ° C. wear resistance ratio of martensitic steel with N as the basic composition and the Nb amount varied. When the Nb addition amount is from 0 to 0.03%, the 350 ° C. wear resistance ratio does not change much, but when the Nb addition amount exceeds 0.03%, the 350 ° C. wear resistance ratio is greatly improved. Since Nb carbonitride precipitated during rolling suppresses recrystallization and refines the structure, Nb is usually added in an amount of 0.01 to 0.02% for this purpose. However, Nb carbonitride deposited during rolling does not contribute much to high temperature hardness. On the other hand, Nb existing in a solid solution state in the steel sheet remains in a solid solution state at 300 ° C. to 400 ° C. or exists as a very fine carbonitride, and any of them contributes to an improvement in high temperature hardness. Inferred. That is, when the steel sheet is heated to 350 ° C. by adding Nb in an amount that greatly exceeds the amount precipitated during rolling and by increasing the solid solution Nb in the steel sheet by selecting appropriate rolling and cooling conditions. It is considered that the hardness can be increased, and as a result, the 350 ° C. wear resistance can be improved.

The inventors analyzed in detail the relationship between the alloying elements and the 350 ° C. wear resistance of more martensitic steels having a HB in the range of 360 to 440 at 25 ° C. As a result, the following formula (1) for predicting the 350 ° C. wear resistance ratio from the chemical composition was derived.
HI = [C] +0.59 [Si] −0.58 [Mn] +0.29 [Cr] +0.39 [Mo] +2.11 ([Nb] −0.02) −0.72 [Ti] +0 56 [V] (1)
Here, [C], [Si], [Mn], [Cr], [Mo], [Nb], [Ti], and [V] are C, Si, Mn, Cr, Mo, Nb, It is content (mass%) of Ti and V. In the formula (1), 0.02 is reduced in the Nb term because the amount precipitated during rolling is taken into consideration.

FIG. 2 shows the relationship between HI and the 350 ° C. wear resistance ratio of martensitic steel.
The target value of the high temperature wear resistance in the present invention is set such that the 350 ° C. wear resistance ratio is 3.0 or more, that is, the wear loss is 1/3 or less of SS400. In order to satisfy this target value, it can be seen from the relationship in FIG. 2 that HI should be 0.7 or more. Furthermore, when the HI is 0.8 or more, the wear resistance ratio is 4.0 or more, and a better wear resistance can be obtained.

According to the formula (1), it is effective to add a large amount of Si, Cr, Mo and V in addition to Nb to improve the 350 ° C. wear resistance of the martensitic steel.
Of these, Mo and V are elements that have been widely used in high temperature steels in the past, but the price has soared in recent years, and it is desirable to reduce the addition amount as much as possible from the viewpoint of economy. .
On the other hand, since Si and Cr are relatively inexpensive elements, it can be said that they are advantageous elements for improving the 350 ° C. wear resistance. Moreover, it is more advantageous for 350 ° C. wear resistance to reduce Mn rather.
On the other hand, in order to obtain a martensite structure up to the center of the plate thickness, it is necessary to ensure sufficient hardenability. The applied plate thickness of wear-resistant steel is often up to 50 mm. If the following Ceq is more than 0.50, it is possible to ensure hardenability sufficient to obtain a martensite structure up to the center of a steel plate having a thickness of 50 mm.
Ceq = [C] + [Si] / 24 + [Mn] / 6 + [Ni] / 40 + [Cr] / 5 + [Mo] / 4 + [V] / 14
Here, [C], [Si], [Mn], [Ni], [Cr], [Mo], and [V] contain C, Si, Mn, Ni, Cr, Mo, and V, respectively. Amount (% by mass).

  Further, regarding the toughness, in order to set the Charpy absorbed energy at −40 ° C. to 27 J or more, it is necessary to appropriately regulate the upper limit of the contents of Si, P, S, Cr, Mo, Al, B, and N. .

This invention is made | formed based on these knowledge, The place made into the summary is as follows.
(1) The wear-resistant steel sheet having excellent high-temperature wear resistance and bending workability according to the present invention is in mass%, C: 0.13% or more, 0.18% or less, Si: 0.5% or more, 1.0 %, Mn: 0.2% or more, 0.8% or less, P: 0.020% or less, S: 0.010% or less, Cr: 0.5% or more, 2.0% or less, Mo: 0 0.03% or more, 0.30% or less, Nb: more than 0.03%, 0.10% or less, Al: 0.01% or more, 0.20% or less, B: 0.0005% or more, 0.0030 %, N: 0.010% or less, Fe and unavoidable impurities as the balance, the composition of the following HI is 0.7 or more, and Ceq is more than 0.50 And HB (Brinell hardness) is 360 or more and 440 or less at 25 ° C.
HI = [C] +0.59 [Si] −0.58 [Mn] +0.29 [Cr] +0.39 [Mo] +2.11 ([Nb] −0.02) −0.72 [Ti] +0 .56 [V]
Ceq = [C] + [Si] / 24 + [Mn] / 6 + [Ni] / 40 + [Cr] / 5 + [Mo] / 4 + [V] / 14
Here, [C], [Si], [Mn], [Ni], [Cr], [Mo], [Nb], [Ti], and [V] are C, Si, Mn, Ni, It is content (mass%) of Cr, Mo, Nb, Ti, and V.
(2) In the wear-resistant steel sheet having excellent high-temperature wear resistance and bending workability according to the present invention described in (1), Cu: 0.05% or more, 1.5% or less, Ni: 0.05% or more, 1.0% or less, Ti: 0.003% or more, 0.03% or less, and V: 0.01% or more, 0.20% or less You may contain.

(3) The method for producing a wear-resistant steel sheet having excellent high-temperature wear resistance and bending workability according to the present invention comprises heating a steel slab or slab having the composition described in (1) or (2) above 1200 ° C. The hot rolling is performed at a cumulative reduction ratio of 30% or more and 65% or less at 960 ° C. or lower and 900 ° C. or higher, and the hot rolling is finished at 900 ° C. or higher. Accelerated cooling to 200 ° C. or lower so that the temperature is 5 ° C./s or higher, or after re-heating to 200 ° C. or lower after completion of hot rolling, reheating to a temperature higher than the Ac3 transformation point, Accelerated cooling to 200 ° C. or lower so as to be 5 ° C./s or higher.

  According to the present invention, it has HB400 class room temperature hardness with good bending workability, and has high wear resistance even in a high temperature environment from 300 ° C. to 400 ° C., and is also excellent in economic efficiency. A wear-resistant steel plate can be easily manufactured.

FIG. 1 is a graph showing the relationship between the amount of Nb added and the wear resistance at 350.degree. FIG. 2 is a graph showing the relationship between HI and wear resistance at 350 ° C.

Hereinafter, the present invention will be described in detail.
First, the reasons for limiting the steel components of the wear-resistant steel sheet of the present invention will be described.
C is an important element that determines the hardness of martensite. In the present invention, the C range is 0.13% or more and 0.18% or less in order to set the room temperature HB at the center of the plate thickness up to 50 mm to 360 to 440.
Si is an element particularly effective for improving the 350 ° C. wear resistance, and the alloy price is also low. However, addition of a large amount of Si reduces toughness and processability. For these reasons, the Si addition amount is set to 0.50% or more and less than 1.0%. In the case where workability is more important, the Si addition amount is desirably less than 0.8%.

  Mn is essential in order to avoid a decrease in toughness or bending workability due to segregation of grain boundaries of S by forming MnS, and 0.2% or more is added. Since Mn improves hardenability, it is better to add Mn in order to ensure the normal temperature hardness at the center of the plate thickness up to 50 mm. However, on the other hand, Mn lowers the high-temperature strength, so it rather lowers the 350 ° C. wear resistance. For this reason, the amount of Mn added is desirably less than 0.5%. For the purpose of improving hardenability, the upper limit is made 0.8%. Therefore, the amount of Mn added is 0.2% or more and 0.8% or less, desirably 0.2% or more and less than 0.5%.

  P is an unavoidable impurity that is a harmful element that reduces bending workability and toughness. Therefore, the content is suppressed to 0.020% or less. More desirably, the content is 0.010% or less. P is preferably as low as possible for bending workability and toughness, but an increase in refining cost is inevitable in order to reduce it to less than 0.0005%. Therefore, it is necessary to limit P to such a very low level. Absent.

  S is also an inevitable impurity and is a harmful element that lowers bending workability and toughness. Therefore, the content is suppressed to 0.010% or less. More desirably, the content is 0.005% or less. S is preferably as low as possible for bending workability and toughness, but an increase in refining cost is inevitable in order to reduce it to less than 0.0005%, so it is necessary to limit it to such a very low level. Absent.

  Cr improves the hardenability and is effective for improving the 350 ° C. wear resistance, so at least 0.5% or more is added. In order to obtain sufficient hardenability at the center of the plate thickness up to a plate thickness of 50 mm, the addition amount is desirably 1.0% or more. However, if added excessively, the toughness may be lowered, so the content is made 2.0% or less.

  Mo has the effect of improving the wear resistance at 350 ° C. and greatly increasing the hardenability by adding a small amount in the presence of Nb. Therefore, addition of 0.03% or more is essential. However, if excessively added, the toughness may be lowered, so the upper limit of the amount of Mo added is 0.30%. Moreover, Mo is very expensive in recent years, and the addition amount is preferably less than 0.10% from the viewpoint of suppressing alloy costs.

  Nb is very effective in improving the 350 ° C. wear resistance because it exists in a solid solution state in the steel sheet. The amount of Nb added to ensure sufficient solute Nb is more than 0.03%, and more preferably 0.04% or more. In the present invention, 0.1% or more of C is contained in order to ensure a Brinell hardness HB360 or more at room temperature, so that if Nb content is large, Nb (CN) may not be sufficiently dissolved at the time of heating. Such undissolved Nb does not contribute to improving the high temperature hardness and may cause a decrease in toughness. Therefore, the Nb addition amount is set to 0.10% or less, and more desirably 0.08% or less.

  Al is added in an amount of 0.01% or more as a deoxidizing element or an inclusion form controlling element. Moreover, in order to secure the free B necessary for improving the hardenability, 0.05% or more is added for the purpose of fixing N. In either case, excessive addition may reduce toughness, so the upper limit is made 0.20%, preferably 0.10%.

  B is an essential element that is very effective for improving hardenability. In order to exert the effect, 0.0005% or more is necessary, but if added over 0.0030%, weldability and toughness may be lowered, so the B content is 0.0005% or more, 0 0030% or less.

  If N is contained excessively, it lowers toughness and forms BN to inhibit the effect of improving the hardenability of B, so the content is suppressed to 0.010% or less. More desirably, it is 0.006% or less. N is preferably as low as possible in order to avoid toughness and BN formation, but in order to reduce it to less than 0.001%, an increase in refining cost is inevitable, so it is necessary to limit to such a very low level. Absent.

The above are the basic components of steel in the present invention. In addition, in the present invention, one or more of Cu, Ni, V and Ti can be added in addition to the above components.
Cu is an element that can improve hardness without reducing toughness, and may be added in an amount of 0.05% or more for that purpose. However, if too much Cu is added, the toughness may be lowered, so the addition amount is 1.5% or less.
Ni is an effective element for improving toughness, and 0.05% or more may be added for the purpose. However, since Ni is an expensive element, the addition is made 1.0% or less.

V is an element effective for improving the 350 ° C. wear resistance. For this purpose, 0.01% or more may be added. However, V is also an expensive element, and if added excessively, the toughness may be lowered. Therefore, even when added, the content is made 0.20% or less.
Ti may be added so as to prevent formation of BN by fixing N as TiN and to secure free B necessary for improving hardenability. For this purpose, 0.003% or more is added. Added. However, the addition of Ti tends to lower the 350 ° C. wear resistance. Therefore, the amount of Ti added is 0.030% or less.

  In addition to the above component range limitation, as described above, in the present invention, the component composition is limited so that the HI of formula (1) is 0.7 or more and Ceq is more than 0.50. However, if HI or Ceq is too high, the toughness may be lowered. Therefore, it is desirable that HI is 1.2 or less and Ceq is 0.70 or less.

Next, the manufacturing method of the wear-resistant steel plate of the present invention will be described.
First, hot rolling is performed by heating a steel slab (slab) or slab having the above steel composition.
In the present invention, the method for producing a steel slab or slab prior to hot rolling is not particularly limited. In other words, following smelting with a blast furnace, converter, electric furnace, etc., the components are adjusted so that the desired component content is obtained by various secondary scouring, and then, in addition to normal continuous casting, casting by ingot method, thin slab What is necessary is just to cast by methods, such as casting. Scrap may be used as a raw material. In the case of a slab obtained by continuous casting, it may be directly sent to a hot rolling mill as it is a high-temperature slab, or may be hot-rolled after being reheated in a heating furnace after being cooled to room temperature. The components of the steel slab or slab are the same as the components of the wear-resistant steel plate of the present invention described above.

The heating temperature of the steel slab or slab is set to 1200 ° C. or higher so that Nb is sufficiently dissolved. However, if the heating temperature is too high, the austenite structure becomes coarse, and therefore the structure after hot rolling may not be sufficiently refined and the toughness may be lowered. Therefore, the heating temperature of the steel slab or slab is 1350 ° C. or less. Is desirable.
In hot rolling, the cumulative rolling reduction is set to 30% to 65% at 960 ° C. or lower and 900 ° C. or higher. In order to minimize the precipitation of Nb carbonitride during rolling, it is limited to this temperature and rolling reduction range.
Further, in order to avoid unnecessary Nb carbonitride precipitation and leave a large amount of solid solution Nb, the hot rolling is finished at 900 ° C. or higher. Moreover, the end temperature of hot rolling needs to be 960 degrees C or less.

In order to obtain a martensite structure after hot rolling, accelerated cooling is performed by direct quenching or reheating quenching.
In the case of direct quenching, accelerated cooling is performed immediately after the hot rolling to a temperature of 200 ° C. or less at a cooling rate of 5 ° C./s or more (cooling rate at the center of the plate thickness).
In the case of reheating and quenching, after completion of hot rolling, it is once cooled to a temperature of 200 ° C. or less (the cooling rate at this time is arbitrary), and then reheated to a temperature not lower than the Ac3 transformation point. Accelerated cooling to 200 ° C. or lower so that the cooling rate at the part is 5 ° C./s or higher.
The cooling rate in accelerated cooling after completion of hot rolling in the case of direct quenching and in accelerated cooling after reheating in the case of reheating quenching increases as the plate thickness decreases. In the present application, the target plate thickness is mainly assumed to be about 4.5 mm to 50 mm. Although the cooling rate at a plate thickness of 4.5 mm may become very large, there is no particular problem, and no upper limit is set for the cooling rate.
Tempering heat treatment is not particularly required, but the properties of the steel sheet do not depart from the present invention even if heat treatment is performed at a temperature of 300 ° C. or lower.

  Steel strips obtained by melting steels A to AI having the compositions shown in Tables 1 and 2 were heated to 1230 ° C. or higher, and then in the respective production conditions shown in Tables 3 and 4, the plate thickness was 6 to 45 mm. The steel plate was manufactured. (Steel plates No. 1 to 17 are examples of the present invention, and steel plates No. 18 to 44 are comparative examples)

About these steel plates, normal temperature hardness, the abrasion resistance in 350 degreeC, bending workability, and toughness were evaluated.
About room temperature hardness, it measured at 25 degreeC with the Brinell hardness test method (JISZ2243). The target value of the normal temperature hardness is HB360 or more and HB440 or less.
As described above, the wear resistance ratio is determined by performing a wear test at a sample temperature of 350 ° C. in a pin-on-disk type wear test apparatus compliant with ASTM G99-05, and using SS400 as a standard sample. Wear amount / wear amount of the test sample). The target value of wear resistance is an abrasion resistance ratio of 3.0 or more.
Evaluation of bending workability was performed as follows. By the method prescribed in JIS Z 2248, the test piece JIS No. 1 was bent 180 degrees in the C direction at a bending radius (4 t) four times the plate thickness, and the outside of the curved portion was observed after the bending test. The test was accepted when no tears or other defects occurred outside the curved portion.
The toughness was evaluated as follows. A JIS Z 2201 No. 4 Charpy test piece was sampled at right angles to the rolling direction from the center of the plate thickness, and subjected to an impact test at -40 ° C to measure the absorbed energy value. And the average value of the absorbed energy value of the impact test in -40 degreeC of three test pieces was calculated | required. The average value of the toughness target value was set to 27 J or more.
The obtained results are shown in Tables 5 and 6.
In Tables 1 to 6, numerical values with an underline indicate component values outside of the present invention, temperature conditions, and characteristics that are insufficient.

  In the steel plates Nos. 1 to 17 of the inventive examples in Table 5, all of the above-mentioned normal temperature hardness, wear resistance at 350 ° C., bending workability, and toughness target values are satisfied. On the other hand, in steel plate Nos. 18 to 40, which are comparative examples of steel components that deviate from the chemical composition range limited by the present invention, although the manufacturing method is the method of the present invention, the normal temperature hardness is 350 ° C. One or more of the wear resistance, bending workability, and toughness of the steel is less than the target value. Also in the steel plates Nos. 41 to 44 of the comparative examples which are the steel components of the present invention but deviate from the production method of the present invention, among the normal temperature hardness, wear resistance at 350 ° C., bending workability, and toughness One or more are rejected.

  According to the present invention, a wear-resistant steel sheet having HB400 class room temperature hardness with good bending workability, high wear resistance even in a high temperature environment of 300 ° C. to 400 ° C., and excellent in economic efficiency. Can be easily manufactured. For this reason, it is suitable for parts such as construction machinery and industrial machinery that require high wear resistance in high temperature environments such as bulldozer buckets that generate frictional heat due to strong impacts and sintered coke hoppers that collide with high-temperature objects. Available.

Claims (3)

% By mass
C: 0.13% or more, 0.18% or less,
Si: 0.5% or more and less than 1.0%,
Mn: 0.2% or more, 0.8% or less,
P: 0.020% or less,
S: 0.010% or less,
Cr: 0.5% or more, 2.0% or less,
Mo: 0.03% or more, 0.30% or less,
Nb: more than 0.03%, 0.10% or less,
Al: 0.01% or more, 0.20% or less,
B: 0.0005% or more, 0.0030% or less, and N: 0.010% or less,
Containing Fe and inevitable impurities as the balance,
The component composition satisfies that the following HI is 0.7 or more and Ceq is more than 0.50,
A wear-resistant steel sheet having excellent high-temperature wear resistance and bending workability, characterized in that HB (Brinell hardness) is 360 or more and 440 or less at 25 ° C.
HI = [C] +0.59 [Si] −0.58 [Mn] +0.29 [Cr] +0.39 [Mo] +2.11 ([Nb] −0.02) −0.72 [Ti] +0 .56 [V]
Ceq = [C] + [Si] / 24 + [Mn] / 6 + [Ni] / 40 + [Cr] / 5 + [Mo] / 4 + [V] / 14
Here, [C], [Si], [Mn], [Ni], [Cr], [Mo], [Nb], [Ti], and [V] are C, Si, Mn, Ni, It is content (mass%) of Cr, Mo, Nb, Ti, and V.   Further, by mass, Cu: 0.05% or more, 1.5% or less, Ni: 0.05% or more, 1.0% or less, Ti: 0.003% or more, 0.03% or less, and V The wear-resistant steel sheet having excellent high-temperature wear resistance and bending workability according to claim 1, characterized by containing one or more of 0.01% or more and 0.20% or less. A steel slab or slab having the composition according to claim 1 or 2 is heated to 1200 ° C or higher, and hot rolling is performed at a cumulative reduction of 30% to 65% at 960 ° C or lower and 900 ° C or higher, Finish hot rolling at 900 ° C or higher,
After completion of hot rolling, it is accelerated to 200 ° C. or less so that the cooling rate at the center of the sheet thickness is 5 ° C./s or more, or after cooling to 200 ° C. or less after completion of hot rolling, the Ac3 transformation point or more. Reheating to temperature, accelerated cooling to 200 ° C. or lower so that the cooling rate at the center of the plate thickness is 5 ° C./s or higher, producing a wear-resistant steel plate with excellent high temperature wear resistance and bending workability Method.

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