CN115667562A - Wear-resistant steel sheet and method for producing wear-resistant steel sheet - Google Patents

Wear-resistant steel sheet and method for producing wear-resistant steel sheet Download PDF

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Publication number
CN115667562A
CN115667562A CN202180036373.2A CN202180036373A CN115667562A CN 115667562 A CN115667562 A CN 115667562A CN 202180036373 A CN202180036373 A CN 202180036373A CN 115667562 A CN115667562 A CN 115667562A
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steel sheet
wear
hardness
less
resistant steel
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木津谷茂树
高山直树
横田智之
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JFE Steel Corp
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JFE Steel Corp
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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Abstract

The invention provides a wear-resistant steel sheet having both excellent wear resistance and wide bending workability. The wear-resistant steel sheet has a predetermined composition, wherein the volume fraction of martensite at a depth of 1mm from the surface is 90% or more, the hardness at a depth of 1mm from the surface is 420 to 560HBW 10/3000 in terms of Brinell hardness, the widthwise hardness difference in hardness at a depth of 1mm from the surface is 30Hv10 or less in terms of Vickers hardness, and the widthwise hardness difference is defined as the difference between two points adjacent at a distance of 10mm in the widthwise direction of the sheet.

Description

Wear-resistant steel sheet and method for producing wear-resistant steel sheet
Technical Field
The present invention relates to an abrasion-resistant steel sheet (abrasion-resistant steel sheet), and more particularly to an abrasion-resistant steel sheet excellent in wide-width bending workability suitable for use as a member of industrial machinery and transportation equipment used in the fields of construction, civil engineering, mining, and the like. The present invention also relates to a method for producing the wear-resistant steel sheet. Here, the broad bending workability means bending workability of 200mm or more in steel sheet width which is a problem in practical use.
Background
It is known that the wear resistance of steel materials is improved by increasing the hardness. Therefore, a steel material having a high hardness by heat treatment such as quenching is used for a member which is worn by sand, rock, or the like.
For example, patent document 1 describes a method of manufacturing a wear-resistant thick steel plate by hot rolling a steel material having a predetermined composition to form a thick steel plate and then quenching the thick steel plate. According to the method described in cited document 1, by controlling the contents of C, alloying elements, and N, a wear-resistant thick steel plate having hardness of 340HB or more and high toughness in a quenched state and improved low-temperature cracking properties of a welded portion can be obtained.
Patent document 2 describes a method for producing a wear-resistant steel sheet by subjecting a steel having a predetermined composition to hot rolling at a reduction ratio of 15% or more at a temperature of 900 ℃ to the Ar3 transformation point, and then directly quenching the steel from a temperature of the Ar3 transformation point or more. According to the method described in cited document 2, a wear-resistant steel sheet having high hardness can be easily obtained by controlling the composition of components and the quenching conditions.
In the above-described techniques described in patent documents 1 and 2, wear resistance is improved by increasing hardness. On the other hand, in order to apply the steel to various shapes of parts and reduce the number of welded portions, there is an increasing demand for wear-resistant steel having excellent bending workability as well as wear resistance.
In response to such a demand, for example, patent document 3 proposes a composition containing C:0.05 to 0.20%, mn:0.50 to 2.5% and Al:0.02 to 2.00% and an area fraction of martensite of 5 to 50%. According to patent document 3, a wear-resistant steel excellent in workability and weldability can be obtained by heating a hot-rolled steel to a temperature in the ferrite-austenite two-phase region between Ac1 and Ac3 points and then quenching the steel to control the area fraction of martensite.
Patent document 4 proposes a method for producing a wear-resistant steel sheet, which comprises: immediately after hot rolling, a steel having a prescribed composition is cooled to Ms point. + -. 25 ℃, the cooling is interrupted and reheated to Ms point +50 ℃ or higher, and then cooled to room temperature. According to the cited document 4, the minimum hardness of the steel sheet obtained by the above-described manufacturing method in the region from the surface to the depth of 5mm is lower by 40HV or more than the maximum hardness of the further inner region of the steel sheet, and as a result, the bending workability is improved.
Further, patent document 5 proposes a method for producing a wear-resistant steel sheet, which comprises: a steel having a predetermined composition and a DI (hardenability index) of 60 or more is hot-rolled, and then cooled to a temperature range of 400 ℃ or less at an average cooling rate of 0.5 to 2 ℃/sec. According to patent document 5, in the wear-resistant steel sheet obtained by the above-mentioned production method, ti-based carbide having an average grain size of 0.5 to 50 μm or more is precipitated at 400 grains/mm 2 As a result, the wear-resistant steel having both excellent wear resistance and bending workability can be obtained without performing heat treatment.
Documents of the prior art
Patent literature
Patent document 1: japanese laid-open patent publication No. 63-1699359
Patent document 2: japanese patent laid-open publication No. Sho 64-031928
Patent document 3: japanese patent laid-open publication No. H07-090477
Patent document 4: japanese patent laid-open publication No. 2006-104489
Patent document 5: japanese patent laid-open No. 2008-169443
Disclosure of Invention
As described in patent documents 3 to 5, conventional methods for improving the bending workability of a wear-resistant steel plate are based on the following idea: the hardness of the matrix phase (matrix) of the steel sheet is suppressed to ensure bending workability, and the microstructure and precipitated carbides are controlled to improve wear resistance. Therefore, it is difficult to sufficiently increase the hardness of the matrix phase by these methods, and the abrasion resistance and the bending workability cannot be simultaneously achieved.
On the other hand, since the level of requirements for abrasion resistance has been increasing year by year, a technique capable of satisfying both of the contradictory properties of abrasion resistance and bending workability at a high level has been demanded.
In the case of processing a wear-resistant steel sheet to produce a member for civil engineering and construction equipment or the like as a final product, bending is generally performed under the condition that the sheet width of the wear-resistant steel sheet is 200mm or more. In general, since bending cracks are more likely to occur as the sheet width is wider, in order to evaluate the bending workability of a steel sheet in actual use, evaluation should be made using a steel sheet having a sheet width of 200mm or more. However, in the conventional techniques described above, the bending workability of a sheet having a width of 200mm or more is not considered.
An object of the present invention is to solve the above problems and to provide a wear-resistant steel sheet having both of two opposite properties of excellent wear resistance and bending workability. In particular, the object of the present invention is to provide a wear-resistant steel sheet excellent in bending workability under severe conditions in which the steel sheet has a width of 200mm or more (hereinafter referred to as "wide bending workability").
The present inventors have studied various factors affecting the wide bending workability of a wear-resistant steel sheet in order to achieve the above object, and as a result, have obtained the following findings (1) to (4).
(1) The hardness and ductility of the surface layer portion of the wear-resistant steel sheet greatly affect the bending workability of the wear-resistant steel sheet.
(2) In particular, if a hard portion or a soft portion is locally present in the wear-resistant steel sheet, strain concentrates around the soft portion or the hard portion, and ductility decreases, and therefore broad bending workability decreases.
(3) By reducing the hardness difference in the wear-resistant steel sheet, the wide bending workability can be improved without reducing the hardness of the matrix phase that significantly affects the wear resistance.
(4) In the production of wear-resistant steel sheets, quenching is performed from the austenite temperature region, and the difference in cooling rate in the width direction of the steel sheet during the quenching is reduced, whereby the difference in hardness of the wear-resistant steel sheets can be reduced.
The present invention has been completed based on the above findings and further research. The gist of the present invention is as follows.
1. A wear-resistant steel sheet having the following composition: comprises by mass%: c:0.15 to 0.30%, si:0.05 to 1.00%, mn:0.50 to 2.00%, P:0.020% or less, S:0.010% or less, al:0.01 to 0.06%, cr:0.10 to 1.00% and N:0.0100% or less, the remainder being Fe and unavoidable impurities;
the volume fraction of martensite at a depth of 1mm from the surface is 90% or more,
the hardness of the steel plate at the depth of 1mm from the surface is 420-560HBW 10/3000 in Brinell hardness,
the difference in hardness in the width direction of the hardness at a depth of 1mm from the surface, defined as the difference between two points adjacent at an interval of 10mm in the plate width direction, is 30Hv10 or less in terms of Vickers hardness.
2. The wear-resistant steel sheet as claimed in claim 1, wherein the composition further contains, in mass%: 0.005 to 0.020%, ti: 0.005-0.020% and B: 0.0003-0.0030% of 1 or more than 2.
3. The wear-resistant steel sheet as claimed in claim 1 or 2, wherein the composition further contains, in mass%, a component selected from the group consisting of Cu:0.01 to 0.5%, ni:0.01 to 3.0%, mo:0.1 to 1.0%, V:0.01 to 0.10%, W:0.01 to 0.5% and Co: 0.01-0.5% of 1 or more than 2.
4. The wear-resistant steel sheet as claimed in any one of claims 1 to 3, wherein the composition further contains, in mass%, a component selected from the group consisting of Ca:0.0005 to 0.0050%, mg:0.0005 to 0.0100% and REM: 0.0005-0.0200% of 1 or more than 2.
5. A method for producing a wear-resistant steel sheet, comprising heating a steel blank having a composition containing, in mass%, C:0.15 to 0.30%, si:0.05 to 1.00%, mn:0.50 to 2.00%, P:0.020% or less, S:0.010% or less, al:0.01 to 0.06%, cr:0.10 to 1.00% and N:0.0100% or less, the remainder being Fe and unavoidable impurities;
hot rolling the heated billet to produce a hot-rolled steel sheet,
the above hot rolled steel sheet is subjected to quenching,
the above quenching is
(a) Direct quenching for cooling the hot-rolled steel sheet from a cooling start temperature of the Ar3 transformation point or more to a cooling stop temperature of the Mf point or less; or
(b) A reheating and quenching step of cooling the hot-rolled steel sheet, reheating the cooled hot-rolled steel sheet to a reheating temperature of at least the Ac3 transformation point and at most 950 ℃, and cooling the reheated hot-rolled steel sheet from the reheating temperature to a cooling stop temperature of at most the Mf point;
the difference between the average cooling rate at the widthwise central position and the average cooling rate at the widthwise 1/4 position of the hot-rolled steel sheet during the cooling process of quenching is 5 ℃/sec or less, and the difference between the average cooling rate at the widthwise central position and the average cooling rate at the widthwise 3/4 position thereof is 5 ℃/sec or less.
6. The method for producing a wear-resistant steel sheet as described in the above 5, wherein the cooling stop temperature in the quenching is lower than (Mf point-100 ℃ C.),
after the quenching, the quenched hot-rolled steel sheet is tempered at a tempering temperature of (Mf point-80 ℃) to (Mf point +50 ℃).
7. The method for producing a wear-resistant steel sheet according to claim 6, wherein the tempering is performed while the steel sheet is kept at the tempering temperature for 60 seconds or more.
8. The method for producing a wear-resistant steel sheet according to claim 6 or 7, wherein an average temperature increase rate in the tempering is 2 ℃/sec or more.
9. The method for producing a wear-resistant steel sheet as described in the above 5, wherein the cooling stop temperature in the quenching is Mf point or lower and (Mf point-100 ℃ C.) or higher,
after the quenching, the quenched hot-rolled steel sheet is air-cooled.
10. The method for producing a wear-resistant steel sheet according to any one of claims 5 to 9, wherein the composition further contains, in mass%, a chemical composition selected from the group consisting of Nb:0.005 to 0.020%, ti: 0.005-0.020% and B: 0.0003-0.0030% of 1 or more than 2.
11. The method for producing a wear-resistant steel sheet according to any one of the above 5 to 10, wherein the composition further contains, in mass%, a component selected from the group consisting of Cu:0.01 to 0.5%, ni:0.01 to 3.0%, mo:0.1 to 1.0%, V:0.01 to 0.10%, W:0.01 to 0.5% and Co: 0.01-0.5% of 1 or more than 2.
12. The method for producing a wear-resistant steel sheet as claimed in any one of the above 5 to 11, wherein the above composition further contains, in mass%, a component selected from the group consisting of Ca:0.0005 to 0.0050%, mg:0.0005 to 0.0100% and REM: 0.0005-0.0200% of 1 or more than 2.
According to the present invention, a wear-resistant steel sheet having both excellent wear resistance and wide bending workability can be produced. According to the present invention, excellent wide bending workability can be achieved without lowering the hardness that affects wear resistance, and therefore, the present invention can also meet the recent high level of demand for wear resistance. Therefore, the wear-resistant steel sheet of the present invention can be suitably used as a material for parts of industrial machines and conveying facilities used in the fields of construction, civil engineering, mines, and the like.
Detailed Description
Hereinafter, the method for carrying out the present invention will be specifically described. The following description shows examples of preferred embodiments of the present invention, but the present invention is not limited to these examples.
[ composition of ingredients ]
In the present invention, it is important that the wear-resistant steel sheet and the steel blank used for the production thereof have the above-described composition. Therefore, the reason why the composition of the steel is limited as described above in the present invention will be described first. Note that "%" with respect to the composition of components means "% by mass" unless otherwise specified.
C：0.15～0.30％
C is an element for increasing the hardness of the matrix phase and improving the wear resistance. In order to obtain this effect, the C content is set to 0.15% or more. The C content is preferably 0.20% or more. On the other hand, if the C content exceeds 0.30%, the hardness of the matrix phase excessively increases, and the broad bending workability significantly decreases. Therefore, the C content is 0.30% or less. The C content is preferably 0.28% or less.
Si：0.05～1.00％
Si is an element that functions as a deoxidizer. Si has an effect of increasing the hardness of the matrix phase by solid-solution strengthening in steel. When the Si content is less than 0.05%, a sufficient deoxidation effect cannot be obtained, the amount of inclusions increases, and as a result, ductility decreases. Therefore, the Si content is set to 0.05% or more. The Si content is preferably 0.10% or more, more preferably 0.20% or more. On the other hand, if the Si content exceeds 1.00%, the amount of inclusions increases, ductility decreases, and as a result, broad bending workability decreases. 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.
Mn：0.50～2.00％
Mn is an element that increases the hardness of the matrix phase and improves the wear resistance. If the Mn content is less than 0.50%, hardenability is insufficient, and uniform hardness cannot be obtained. Therefore, the Mn content is set to 0.50% or more. The Mn content is preferably 0.60% or more, more preferably 0.70% or more. On the other hand, if the Mn content exceeds 2.00%, the hardness becomes too high, and therefore the broad bending workability is lowered. Therefore, the Mn content is 2.00% or less. The Mn content is preferably 1.80% or less, more preferably 1.60% or less.
P:0.020% or less
P is an element contained as an inevitable impurity, and is segregated in the grain boundary to cause adverse effects such as becoming a starting point of destruction. Therefore, the P content is preferably reduced as much as possible, but if it is 0.020% or less, it is allowable. The lower limit of the P content is not particularly limited, but it is difficult to reduce the P content to less than 0.001% in industrial-scale production, and therefore, from the viewpoint of productivity, the P content is preferably 0.001% or more.
S:0.010% or less
S is an element contained as an unavoidable impurity, and is an element which is present in steel as a sulfide-based inclusion such as MnS and exerts an adverse effect such as becoming a starting point of fracture. Therefore, it is preferable to reduce the S content as much as possible, but if it is 0.010% or less, it is allowable. The lower limit of the S content is not particularly limited, but it is difficult to reduce the S content to less than 0.0001% in industrial-scale production, and therefore, from the viewpoint of productivity, the S content is preferably 0.0001% or more.
Al：0.01～0.06％
Al is an element that functions as a deoxidizer and has an action of forming a nitride to refine crystal grains and improve ductility. In order to obtain these effects, the Al content is set to 0.01% or more. On the other hand, if the Al content exceeds 0.06%, nitrides are excessively formed, and the generation of surface defects increases. On the other hand, if the Al content exceeds 0.06%, the oxide inclusions increase, the ductility decreases, and as a result, the broad bending workability decreases. Therefore, the Al content is 0.06% or less. The Al content is preferably 0.05% or less, and more preferably 0.04% or less.
Cr：0.10～1.00％
Cr is an element that increases the hardness of the matrix phase and improves wear resistance. When the Cr content is less than 0.10%, the effect of improving hardenability by adding Cr is not obtained, and uniform hardness is not obtained. Therefore, the Cr content is set to 0.10% or more. The Cr content is preferably 0.20% or more, more preferably 0.25% or more. On the other hand, if the Cr content exceeds 1.00%, ductility is reduced by the formation of precipitates, and broad bending workability is reduced. Therefore, the Cr content is 1.00% or less. The Cr content is preferably 0.85% or less, more preferably 0.80% or less.
N:0.0100% or less
N is an element contained as an inevitable impurity, and contributes to grain refinement of crystal grains by forming a nitride or the like. However, if the precipitates are excessively formed, ductility is lowered and broad bending workability is lowered. Therefore, the N content is set to 0.0100% or less. The N content is preferably 0.0060% or less, more preferably 0.0040% or less. The lower limit of the N content is not particularly limited, but it is difficult to reduce the N content to less than 0.0010% in industrial-scale production, and therefore the N content is preferably 0.0010% or more from the viewpoint of productivity.
The wear-resistant steel sheet and the steel blank according to one embodiment of the present invention have the above-described composition and the composition including the remaining Fe and inevitable impurities.
In another embodiment of the present invention, the above-mentioned composition may optionally further contain an additive selected from the group consisting of Nb:0.005 to 0.020%, ti:0.005 to 0.020%, and B: 0.0003-0.0030% of the total amount of 1 or more than 2.
Nb：0.005～0.020％
Nb is an element that increases the hardness of the matrix phase and contributes to further improvement in wear resistance. In addition, nb forms carbonitrides to make austenite grains fine. In the case of adding Nb, the Nb content is set to 0.005% or more, preferably 0.007% or more, in order to obtain the above effects. On the other hand, if the Nb content exceeds 0.020%, nbC precipitates in a large amount, resulting in a reduction in ductility and, as a result, wide bending workability. Therefore, when Nb is added, the Nb content is set to 0.020% or less. The Nb content is preferably 0.018% or less.
Ti：0.005～0.020％
Ti is an element that forms nitrides in steel to make prior austenite grains fine, thereby improving ductility. In addition, when both Ti and B coexist, N is fixed by Ti to suppress precipitation of BN, and as a result, the hardenability improving effect of B is improved. In order to obtain these effects, the content of Ti is set to 0.005% or more when Ti is added. The Ti content is preferably 0.007% or more. On the other hand, if the Ti content exceeds 0.020%, a large amount of hard TiC precipitates, and the broad bending workability is lowered. Therefore, when Ti is contained, the Ti content is 0.020% or less. The Ti content is preferably 0.015% or less.
B：0.0003～0.0030％
B is an element that significantly improves hardenability even when added in a trace amount. Therefore, the addition of B can promote the formation of martensite, thereby effectively improving the wear resistance. In order to obtain this effect, when B is added, the content of B is set to 0.0003% or more. The B content is preferably 0.0005% or more, more preferably 0.0008% or more. On the other hand, if the B content exceeds 0.0030%, adverse effects such as formation of a large amount of precipitates such as borides which become fracture origins occur. Therefore, when B is added, the B content is set to 0.0030% or less. The content of B is preferably 0.0015% or less.
In another embodiment of the present invention, the above-mentioned composition may optionally further contain a metal selected from Cu:0.01 to 0.5%, ni:0.01 to 3.0%, mo:0.1 to 1.0%, V:0.01 to 0.10%, W:0.01 to 0.5% and Co: 0.01-0.5% of 1 or more than 2.
Cu：0.01～0.5％
Cu is an element for improving hardenability, and may be added as needed to further improve hardness. In the case of adding Cu, the Cu content is set to 0.01% or more in order to obtain the above effects. On the other hand, if the Cu content exceeds 0.5%, the alloy cost increases in addition to the reduction in manufacturability such as the generation of surface defects. Therefore, when Cu is added, the Cu content is set to 0.5% or less.
Ni：0.01～3.0％
Ni is an element for improving hardenability, and may be added as needed to further improve hardness. In the case where Ni is added, the Ni content is set to 0.01% or more in order to obtain the above effects. On the other hand, if the Ni content exceeds 3.0%, the alloy cost increases. Therefore, the Ni content is 3.0% or less.
Mo：0.1～1.0％
Mo is an element for improving hardenability, and may be added as needed to further improve hardness. In the case where Mo is added, the Mo content is set to 0.1% or more in order to obtain the effect. On the other hand, if the Mo content exceeds 1.0%, the weldability deteriorates and the alloy cost increases. Therefore, when Mo is added, the Mo content is set to 1.0% or less.
V：0.01～0.10％
V is an element for improving hardenability, and may be added as needed to further improve hardness. V is an element contributing to reduction of dissolved N by precipitation as VN. When V is added, the content of V is set to 0.01% or more in order to obtain the above-mentioned effects. On the other hand, if the amount exceeds 0.10%, ductility decreases due to precipitation of hard VC. Therefore, when V is added, the V content is 0.10% or less, preferably 0.08% or less, and more preferably 0.05% or less.
W：0.01～0.5％
W is an element which improves hardenability in the same manner as Mo, and may be added arbitrarily. In the case of adding W, the W content is set to 0.01% or more in order to obtain the above effects. On the other hand, if the W content exceeds 0.5%, an increase in alloy cost results. Therefore, when W is added, the W content is set to 0.5% or less.
Co：0.01～0.5％
Co is an element for improving hardenability, and may be added arbitrarily. When Co is added, the content of Co is set to 0.01% or more in order to obtain the above effects. On the other hand, if the Co content exceeds 0.5%, the alloy cost increases, so in the case of Co addition, the Co content is made 0.5% or less.
In another embodiment of the present invention, the above-mentioned composition may optionally further contain at least one element selected from the group consisting of Ca:0.0005 to 0.0050%, mg:0.0005 to 0.0100% and REM: 0.0005-0.0200% of 1 or more than 2.
Ca：0.0005～0.0050％
Ca is an element useful for controlling the morphology of sulfide-based inclusions, and may be added arbitrarily. In order to exert its effect, it is necessary to add 0.0005% or more. Therefore, when Ca is added, the Ca content is set to 0.0005% or more. On the other hand, if the amount exceeds 0.0050%, the amount of inclusions in the steel increases, which results in a reduction in ductility and a reduction in broad bending workability. Therefore, when Ca is contained, the content of Ca is set to 0.0050% or less, preferably 0.0025% or less.
Mg：0.0005～0.0100％
Mg is an element that forms a stable oxide at high temperature, effectively suppresses coarsening of prior austenite grains, and improves ductility. In order to exert its effect, it is necessary to add 0.0005% or more. Therefore, when Mg is added, the Mg content is set to 0.0005% or more. On the other hand, if the amount of the additive exceeds 0.0100%, the amount of the inclusions in the steel increases, whereby ductility decreases and broad bending workability decreases. Therefore, when Mg is contained, the Mg content is set to 0.0100% or less, preferably 0.0050% or less.
REM：0.0005～0.0200％
REM (rare earth metal) also has the effect of improving the quality by forming oxides and sulfides in steel in the same manner as Ca, and in order to obtain the effect, 0.0005% or more needs to be added. Therefore, in the case of adding REM, the REM content is made 0.0005% or more. On the other hand, even if more than 0.0200% is added, the effect is saturated. Therefore, when REM is contained, the REM content is 0.0200% or less, preferably 0.0100% or less.
[ microstructure ]
Volume fraction of martensite: over 90 percent
In the present invention, the volume fraction of martensite in the wear-resistant steel sheet at a depth of 1mm from the surface is set to 90% or more. If the volume fraction of martensite is less than 90%, the hardness of the matrix structure of the wear-resistant steel sheet decreases, and therefore the wear resistance deteriorates. Therefore, the volume fraction of martensite is 90% or more. On the other hand, the higher the volume fraction of martensite, the better, so the upper limit of the volume fraction is not particularly limited, and may be 100%. The volume fraction of martensite can be measured by the method described in examples.
If the volume fraction of martensite is 90% or more, the desired wear resistance can be obtained regardless of the structure of the remaining portion, and therefore the structure of the remaining portion other than martensite is not particularly limited and may be any structure. The remaining structure may be 1 or 2 or more kinds selected from ferrite, pearlite, austenite and bainite, for example.
[ hardness ]
Brinell hardness: 420-560HBW 10/3000
The wear-resistant steel sheet of the present invention has a hardness of 420 to 560HBW 10/3000 in terms of Brinell hardness at a depth of 1mm from the surface, in addition to the above-described composition. The reason for limiting the surface hardness is described below.
The wear resistance of the steel sheet can be improved by increasing the hardness of the surface layer portion of the steel sheet. If the hardness at a depth of 1mm from the surface of the steel sheet is less than 420HBW on the Brinell hardness scale, sufficient abrasion resistance cannot be obtained, and the service life in use is shortened. Therefore, the hardness of the steel sheet at a depth of 1mm from the surface is 420HBW or more, preferably 440HBW or more in terms of Brinell hardness. On the other hand, if the hardness at a depth of 1mm from the surface of the steel sheet exceeds 560HBW on a Brinell hardness scale, the broad bending workability deteriorates. Therefore, the hardness of the steel sheet at a depth of 1mm from the surface thereof is 560HBW or less in terms of Brinell hardness. Here, the Brinell hardness is a value (HBW 10/3000) at a position of 1/4 of the plate width measured under a load of 3000kgf using a tungsten hard ball having a diameter of 10mm.
[ difference in hardness in the width direction ]
Difference in width direction hardness: 30Hv10 or less
When a hard portion or a soft portion is locally present in the wear-resistant steel sheet, strain concentrates around the soft portion or the hard portion, and ductility is reduced, so that excellent wide bending workability cannot be obtained. Therefore, in the present invention, the difference in hardness in the width direction of the wear-resistant steel sheet at a depth of 1mm from the surface, defined as the difference between two points adjacent at a distance of 10mm in the sheet width direction, is 30Hv10 or less in terms of vickers hardness. By setting the difference in hardness to the above range, good bending characteristics can be obtained even in wide bending. In addition, since steel sheets are generally manufactured while being moved in the longitudinal direction (rolling direction), if uniformity is maintained in the width direction (direction orthogonal to rolling), the longitudinal direction is also uniform.
The difference in the width direction hardness can be evaluated by measuring the vickers hardness at a position 1mm deep from the surface of the wear-resistant steel sheet in the width direction at intervals of 10mm and determining the difference in hardness between adjacent measurement points. A hardness difference in the width direction of 30Hv10 or less means that the hardness difference between all adjacent two points is 30Hv10 or less, in other words, the maximum value of the hardness difference between adjacent two points is 30Hv10 or less.
In general, thermal cutting such as gas cutting, plasma cutting, and laser cutting is used for cutting the wear-resistant steel sheet. In the wear-resistant steel sheet for hot cutting, the hardness of the end portion changes due to the influence of heat during cutting. Therefore, in the measurement of the difference in hardness in the width direction, the heat-affected zone at the end of the wear-resistant steel sheet is excluded from the measurement target. More specifically, the difference in hardness in the width direction can be determined by measuring the vickers hardness at intervals of 10mm in the width direction within a range excluding the range of 50mm near one side in the width direction of the wear-resistant steel sheet.
If the measurement is performed at intervals of more than 10mm, a change in hardness, which causes deterioration in bending workability, cannot be detected. On the other hand, if the measurement interval is reduced, the detection accuracy of the hardness change is improved, but the number of measurement points becomes huge. Further, as shown in examples described later, it was confirmed that excellent performance was actually obtained by controlling the difference in hardness measured at intervals of 10mm. For the above reasons, the measurement interval was set to 10mm.
[ thickness of plate ]
The thickness of the wear-resistant steel sheet of the present invention is not particularly limited, and may be any thickness. However, since a wear-resistant steel sheet having a thickness of 4 to 60mm is particularly required to have wide bendability, it is preferable to set the thickness of the wear-resistant steel sheet to 4 to 60mm.
[ production method ]
Next, a method for manufacturing a wear-resistant steel sheet according to an embodiment of the present invention will be described. The wear-resistant steel sheet of the present invention can be produced by heating and hot rolling a steel blank having the above-described composition, and then performing heat treatment including quenching under the conditions described below.
[ Steel blank ]
As the steel material, any form of material can be used. The billet may be a billet, for example.
The method for producing the steel material is not particularly limited, but it can be produced by, for example, melting and casting molten steel having the above-described composition by a conventional method. The melting may be performed by any method such as a converter, an electric furnace, or an induction furnace. In addition, the casting is preferably performed by a continuous casting method from the viewpoint of productivity, but may be performed by an ingot casting method.
[ heating ]
The above steel stock is heated to a heating temperature before hot rolling. The heating may be performed after the steel blank obtained by casting or the like is once cooled, or the obtained steel blank may be directly heated without being cooled.
Heating temperature: ac3 transformation point of 1300 ℃ or higher
If the heating temperature is lower than the Ac3 transformation point, a ferrite phase is included in the microstructure of the steel sheet after heating, and therefore, sufficient hardness cannot be obtained after quenching, and the microstructure cannot be made uniform. Therefore, the heating temperature is not lower than the Ac3 transformation point. On the other hand, if the heating temperature is higher than 1300 ℃, excessive energy is required for heating, and thus the manufacturability is degraded. Therefore, the heating temperature is 1300 ℃ or lower, preferably 1250 ℃ or lower, more preferably 1200 ℃ or lower, and further preferably 1150 ℃ or lower.
The Ac3 transformation point can be obtained by the following equation.
Ac3(℃)＝912.0－230.5×C+31.6×Si－20.4×Mn－39.8×Cu－18.1×Ni－14.8×Cr+16.8×Mo
(wherein the element symbols in the above formula represent the content of each element in mass%, and the content of the element not contained is 0.)
[ Hot Rolling ]
Next, the heated steel slab is hot-rolled to produce a hot-rolled steel sheet. The conditions for the hot rolling are not particularly limited, and the hot rolling can be carried out by a conventional method. In the present invention, the hot rolling conditions are not particularly limited in order to control the hardness of the steel sheet and the like in the heat treatment process after hot rolling. However, from the viewpoint of reducing the deformation resistance of the steel material and reducing the load on the rolling mill, the rolling end temperature is preferably 750 ℃ or more, more preferably 800 ℃ or more, and still more preferably 850 ℃ or more. On the other hand, the rolling end temperature is preferably 1000 ℃ or less, more preferably 950 ℃ or less, from the viewpoint of preventing significant coarsening of austenite grains and a reduction in ductility after heat treatment caused thereby.
In the present invention, the hot-rolled steel sheet is subjected to a heat treatment including quenching. The heat treatment may be performed by any of the two embodiments described below. In the following description, the "cooling start temperature" refers to the surface temperature of the steel sheet at the start of cooling in the cooling process of quenching. The "cooling stop temperature" refers to the surface temperature of the steel sheet at the end of cooling in the cooling process of quenching.
In one embodiment of the present invention, the hot-rolled steel sheet obtained after the hot rolling is quenched. The quenching is performed by either (a) Direct Quenching (DQ) or (b) Reheat Quenching (RQ). The cooling method in the quenching is not particularly limited, but is preferably water-cooled.
(a) Direct Quenching (DQ)
In the case where the quenching is performed by direct quenching, the hot-rolled steel sheet after the hot rolling is cooled from a cooling start temperature of the Ar3 transformation point or more to a cooling stop temperature of the Mf point or less.
Cooling start temperature: ar3 transformation point or higher
If the cooling start temperature is not lower than the Ar3 transformation point, quenching is started from the austenite region, and thus a desired martensite structure can be obtained. If the cooling start temperature is lower than the Ar3 point, ferrite is generated, and therefore the volume fraction of martensite in the finally obtained microstructure is lower than 90%. If the volume fraction of martensite is less than 90%, the hardness of the steel sheet cannot be sufficiently increased, and as a result, the wear resistance of the steel sheet is lowered. Further, if the cooling start temperature is lower than the Ar3 point, a difference in hardness occurs in the width direction, and thus the broad bending workability is lowered. On the other hand, the upper limit of the cooling start temperature is not particularly limited, but is preferably 950 ℃ or lower.
The Ar3 transformation point can be obtained by the following equation.
Ar3(℃)＝910－273×C－74×Mn－57×Ni－16×Cr－9×Mo－5×Cu
(wherein, the symbol of the element in the above formula represents the content of each element in mass%, and the content of the element not contained is 0.)
Cooling stop temperature: mf Point or lower
If the cooling stop temperature is higher than the Mf point, the volume fraction of martensite cannot be sufficiently increased, and the desired hardness cannot be obtained. Further, if the cooling stop temperature is higher than the Mf point, a difference in hardness occurs in the width direction, and thus the wide bending workability is lowered. Therefore, the cooling stop temperature is equal to or lower than the Mf point. From the viewpoint of increasing the volume fraction of martensite, the cooling stop temperature is preferably (Mf point-100 ℃) or lower, more preferably (Mf point-120 ℃) or lower, and still more preferably (Mf point-150 ℃) or lower. On the other hand, the lower limit of the cooling stop temperature is not particularly limited, but since excessive cooling lowers the production efficiency, the cooling stop temperature is preferably set to room temperature or higher.
The Mf point can be obtained by the following equation.
Mf(℃)＝410.5－407.3×C－7.3×Si－37.8×Mn－20.5×Cu－19.5×Ni－19.8×Cr－4.5×Mo
(wherein the element symbols in the above formula represent the content of each element in mass%, and the content of the element not contained is 0.)
(b) Reheat Quenching (RQ)
In the case of performing the quenching by reheating quenching, the hot-rolled steel sheet after the hot rolling is first cooled, and the cooled hot-rolled steel sheet is reheated to a reheating temperature of not less than Ac3 transformation point but not more than 950 ℃. Then, the hot-rolled steel sheet after reheating is cooled from the reheating temperature to a cooling stop temperature equal to or lower than the Mf point.
Reheating temperature: ac3 transformation point of 950 ℃ or higher
Since the microstructure can be made austenite by reheating the hot-rolled steel sheet to Ac3 transformation point or higher, the martensite structure can be obtained by quenching (cooling) thereafter. If the reheating temperature is lower than the Ac3 transformation point, ferrite is generated and quenching is insufficient, so that the hardness of the steel sheet cannot be sufficiently increased, and as a result, the wear resistance of the finally obtained steel sheet is lowered. Therefore, the reheating temperature is set to be not lower than the Ac3 transformation point. On the other hand, if the reheating starting temperature is higher than 950 ℃, the crystal grains are coarsened and the workability is degraded. Therefore, the reheating temperature is set to 950 ℃ or lower. In order to start cooling from the reheating temperature, for example, the cooling may be started immediately after the hot-rolled steel sheet comes out of the furnace used for reheating.
Cooling stop temperature: mf point or less
If the cooling stop temperature is higher than the Mf point, the volume fraction of martensite may not be sufficiently increased, and the desired hardness may not be obtained. Further, if the cooling stop temperature is higher than the Mf point, a difference in hardness occurs in the width direction, and thus the broad bending workability is lowered. Therefore, the cooling stop temperature is equal to or lower than the Mf point. From the viewpoint of increasing the volume fraction of martensite, the cooling stop temperature is preferably (Mf point-100 ℃) or lower, more preferably (Mf point-120 ℃) or lower, and still more preferably (Mf point-150 ℃) or lower. On the other hand, the lower limit of the cooling stop temperature is not particularly limited, but since excessive cooling lowers the production efficiency, the cooling stop temperature is preferably set to room temperature or higher.
(average Cooling Rate in quenching)
The cooling rate in the cooling process of the quenching is not particularly limited, and may be any cooling rate as long as the cooling rate forms a martensite phase. For example, the average cooling rate from the start of quenching to the stop of quenching is preferably 10 ℃/sec or more, more preferably 15 ℃/sec or more, and still more preferably 20 ℃/sec or more. On the other hand, the upper limit is not particularly limited, since the higher the average cooling rate in quenching is, in principle, the better. However, since a cooling facility capable of coping with the increase in the cooling rate is required, the average cooling rate is preferably 150 ℃/sec or less, more preferably 100 ℃/sec or less, and still more preferably 80 ℃/sec or less. Here, the average cooling rate is an average cooling rate at the surface temperature of the steel sheet at the center in the width direction. The surface temperature can be measured using a radiation thermometer or the like.
(Cooling Rate Difference)
In the present invention, the difference between the average cooling rate at the widthwise central position and the average cooling rate at the widthwise 1/4 position of the hot-rolled steel sheet and the difference between the average cooling rate at the widthwise central position and the average cooling rate at the widthwise 3/4 position of the hot-rolled steel sheet during the cooling process of quenching are each 5 ℃/sec or less. If the difference in the average cooling rates (hereinafter, sometimes referred to as "cooling rate difference") is greater than 5 ℃/sec, the difference in Vickers hardness between two adjacent points is greater than 30Hv10, and the broad bending workability is deteriorated. Here, the average cooling rate refers to an average cooling rate at the surface temperature of the steel sheet. The surface temperature can be measured using a radiation thermometer or the like.
(tempering)
In one embodiment of the present invention, the quenched hot-rolled steel sheet may be optionally further tempered. By tempering, the uniformity of the hardness of the steel sheet can be further improved. In the case of tempering, the cooling stop temperature in the quenching is preferably lower than (Mf point-100 ℃). After stopping cooling at the cooling stop temperature, the steel sheet may be heated to a tempering temperature described below.
Tempering temperature: (Mf point-80 ℃ C.) - (Mf point +50 ℃ C.)
If the tempering temperature is lower than (Mf point-80 ℃ C.), the tempering effect cannot be obtained. Therefore, when tempering is performed, the tempering temperature is set to (Mf point-80 ℃ C.) or higher, preferably (Mf point-60 ℃ C.) or higher, and more preferably (Mf point-50 ℃ C.) or higher. On the other hand, if the tempering temperature is higher than (Mf point +50 ℃), the reduction in surface hardness becomes significant. Therefore, when tempering is performed, the tempering temperature is set to (Mf Point +50 ℃ C.) or lower, preferably (Mf Point +30 ℃ C.) or lower, and more preferably (Mf Point +10 ℃ C.) or lower.
Temperature maintenance
And stopping heating after the tempering temperature is reached. However, in one embodiment of the present invention, after heating to the tempering temperature, the glass may be further held at the tempering temperature for an arbitrary holding time. The holding time is not particularly limited, but is preferably 60 seconds or more, and more preferably 5 minutes or more, from the viewpoint of enhancing the tempering effect. On the other hand, if the holding time is too long, the hardness of the steel sheet may decrease, and therefore, in the case of temperature holding, the holding time is preferably 60 minutes or less, more preferably 30 minutes or less, and still more preferably 20 minutes or less.
Rate of temperature rise
The temperature increase rate up to the tempering temperature in the tempering is not particularly limited. However, from the viewpoint of productivity, the average temperature increase rate up to the tempering temperature is preferably 0.1 ℃/sec or more, and more preferably 0.5 ℃/sec or more. Further, by setting the average temperature rise rate to 2 ℃/sec or more, carbide is finely precipitated, and as a result, the broad bending workability can be further improved. Therefore, from the viewpoint of further improving the broad bending workability, the average temperature rise rate is preferably 2 ℃/sec or more, more preferably 10 ℃/sec or more. 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 facility for reheating becomes large, and in addition, an increase in energy consumption becomes a problem. Therefore, the average temperature increase rate is preferably 30 ℃/sec or less, and more preferably 25 ℃/sec or less.
The heating (temperature increase) in the tempering may be performed by any method without any particular limitation. For example, at least one method selected from heating using a heat treatment furnace, high-frequency induction heating, and energization heating may be used. In the case of performing the above-described temperature maintenance, it is preferable to perform the reheating and temperature maintenance using a heat treatment furnace. When the average temperature increase rate is 2 ℃/sec or more, the heating to the tempering temperature is preferably performed by high-frequency induction heating or energization heating. On the other hand, when a heat treatment furnace is used, the average temperature rise rate is preferably 10 ℃/sec or less. In addition, the tempering may be performed off-line or on-line.
After heating to the tempering temperature and optionally maintaining the temperature, the heating may be stopped or the temperature may be maintained. The subsequent cooling method is not particularly limited, and one or both of air cooling and water cooling may be used. In one embodiment of the present invention, the steel sheet may be cooled to room temperature after stopping heating or maintaining the temperature.
In another embodiment of the present invention, the cooling in the quenching is interrupted in a specific temperature range, and then air cooling is performed. Thus, since the steel sheet is tempered, the uniformity of the hardness of the steel sheet can be further improved as in the case of tempering in the above embodiment. This embodiment will be described below.
Cooling stop temperature: mf point or less and (Mf point-100 ℃ C.) or more
As described above, if the cooling stop temperature in the quenching is higher than the Mf point, the volume fraction of martensite cannot be sufficiently increased, and the desired hardness cannot be obtained. Further, if the cooling stop temperature is higher than the Mf point, a difference in hardness occurs in the width direction, and thus the wide bending workability is lowered. Therefore, the cooling stop temperature is Mf point or lower. On the other hand, if the cooling stop temperature is lower than (Mf point-100 ℃ C.), the tempering effect cannot be obtained even if air cooling is performed after the cooling stop. Therefore, in the present embodiment, the cooling stop temperature is set to (Mf point-100 ℃ C.) or higher. From the viewpoint of enhancing the tempering effect by air cooling, the cooling stop temperature is preferably (Mf point-80 ℃ C.) or higher, and more preferably (Mf point-50 ℃ C.) or higher.
In the present embodiment, the tempering effect can be obtained by stopping cooling at the cooling stop temperature and then performing air cooling. The air cooling may be performed under any conditions without particular limitation, but the cooling rate is preferably 1 ℃/sec or less.
Examples
In order to confirm the effect of the present invention, a wear-resistant steel sheet was produced according to the following procedure, and the properties thereof were evaluated.
First, molten steel having a composition shown in table 1 was melted to obtain a billet as a billet material. The obtained slabs were heated to the heating temperatures shown in table 2, and then hot-rolled under the conditions shown in table 2 to obtain hot-rolled steel sheets. The obtained hot-rolled steel sheets were subjected to direct quenching or reheat quenching under the conditions shown in table 2 to produce abrasion-resistant steel sheets. In some examples, after quenching, tempering was performed under the conditions shown in table 2. In the example where tempering was not performed, after quenching was stopped, air cooling was performed at a cooling rate of 1 ℃/sec or less.
The column entitled "cooling rate difference" in table 2 indicates the larger value of the difference between the average cooling rate at the widthwise central position and the average cooling rate at the widthwise 1/4 position of the hot-rolled steel sheet, and the difference between the average cooling rate at the widthwise central position and the average cooling rate at the widthwise 3/4 position during the cooling process of quenching.
Next, each of the wear-resistant steel sheets obtained was evaluated for the volume fraction of martensite (M), the hardness, the maximum value of the difference in the widthwise hardness, and the wide bending radius. The evaluation method is as follows.
(volume fraction of martensite)
Samples were taken from the respective steel sheets so that a position 1mm deep from the surface of the steel sheet became an observation position. The surface of the sample was mirror-polished, etched with a nital solution, and then photographed by a Scanning Electron Microscope (SEM) to a range of 10mm × 10mm. The image analysis device analyzes the captured image to determine the area fraction of martensite. The 10 fields were observed at random, and the average of the obtained surface integral ratios was taken as the volume ratio of martensite.
(surface hardness)
From the wear-resistant steel sheet thus obtained, a test piece for hardness measurement was taken, and the Brinell hardness was measured in accordance with the regulations of JIS Z2243 (1998). In order to eliminate the influence of the scale and the decarburized layer present on the surface of the wear-resistant steel sheet, the above measurement was performed after grinding and removing a region of 1mm depth from the surface of the steel sheet. Therefore, the measured hardness is the hardness of the surface at a depth of 1mm from the surface of the steel sheet. The measurement position in the plate width direction is 1/4 of the plate width. In the measurement, a tungsten hard ball having a diameter of 10mm was used, and the load was 3000kgf.
(difference in hardness in the widthwise direction)
The Vickers hardness of the wear-resistant steel sheet was measured at intervals of 10mm in the width direction at a depth of 1mm from the surface. In the above measurement, the regions of 50mm near both ends and one side of the wear-resistant steel sheet were excluded from the measurement range. From the obtained values, the absolute value of the difference in vickers hardness between two adjacent points was obtained, and the maximum value thereof is shown in table 3. The test load in the measurement of the Vickers hardness was 10kg.
(ultimate bend radius)
A bending test piece having a width of 200mm X a length of 300mm was taken from the obtained steel sheet, and bending angles were measured in accordance with JIS Z2248: bending test at 180 deg.. The limit bend radius R/t was determined from the minimum bend radius R (mm) and the sheet thickness t (mm) at which no crack occurred in the above bending test.
The evaluation results obtained by the above methods are shown in table 3. From the results shown in table 3, it is understood that the wear-resistant steel sheet satisfying the conditions of the present invention has a surface hardness of 420HBW 10/3000 or more in terms of brinell hardness and is excellent in wear resistance. The wear-resistant steel sheet satisfying the conditions of the present invention has a limit bending radius R/t of 5.0 or less in the bending test and is excellent in wide bending workability. Thus, the wear-resistant steel sheet of the present invention has both excellent wear resistance and wide bending workability. From the results, it is understood that the present invention can improve the broad bending workability without lowering the surface hardness of the wear-resistant steel sheet.
Figure BDA0003950974880000191
Figure BDA0003950974880000201
[ Table 3]
Figure BDA0003950974880000211

Claims (12)

1. A wear-resistant steel sheet having the following composition: contains, in mass%, C:0.15 to 0.30%, si:0.05 to 1.00%, mn:0.50 to 2.00%, P:0.020% or less, S:0.010% or less, al:0.01 to 0.06%, cr:0.10 to 1.00% and N:0.0100% or less, the remainder being Fe and unavoidable impurities;
the volume fraction of martensite at a depth of 1mm from the surface is 90% or more,
the hardness of the steel plate at the depth of 1mm from the surface is 420-560HBW 10/3000 in Brinell hardness,
the difference in hardness in the width direction of the hardness at a depth of 1mm from the surface, defined as the difference between two points adjacent at an interval of 10mm in the plate width direction, is 30Hv10 or less in terms of Vickers hardness.
2. The abrasion-resistant steel sheet as claimed in claim 1, wherein the composition further contains, in mass%, a metal element selected from the group consisting of Nb:0.005 to 0.020%, ti: 0.005-0.020% and B: 0.0003-0.0030% of 1 or more than 2.
3. The wear-resistant steel sheet as claimed in claim 1 or 2, wherein the composition further contains, in mass%, a metal selected from the group consisting of Cu:0.01 to 0.5%, ni:0.01 to 3.0%, mo:0.1 to 1.0%, V:0.01 to 0.10%, W:0.01 to 0.5% and Co: 0.01-0.5% of 1 or more than 2.
4. The wear-resistant steel sheet according to any one of claims 1 to 3, wherein the composition further contains, in mass%, a component selected from the group consisting of Ca:0.0005 to 0.0050%, mg:0.0005 to 0.0100% and REM: 0.0005-0.0200% of 1 or more than 2.
5. A method for producing a wear-resistant steel sheet, comprising heating a steel blank having a composition containing, in mass%, C:0.15 to 0.30%, si:0.05 to 1.00%, mn:0.50 to 2.00%, P:0.020% or less, S:0.010% or less, al:0.01 to 0.06%, cr:0.10 to 1.00% and N:0.0100% or less, the remainder being Fe and unavoidable impurities;
hot rolling the heated billet to produce a hot rolled steel sheet,
the hot rolled steel sheet is subjected to quenching,
the quenching is as follows:
(a) Direct quenching, cooling the hot-rolled steel sheet from a cooling start temperature above the Ar3 transformation point to a cooling stop temperature below the Mf point; or
(b) A reheating and quenching step of cooling the hot-rolled steel sheet, reheating the cooled hot-rolled steel sheet to a reheating temperature of at least the Ac3 transformation point and at most 950 ℃, and cooling the reheated hot-rolled steel sheet from the reheating temperature to a cooling stop temperature of at most the Mf point;
the difference between the average cooling rate at the widthwise central position and the average cooling rate at the widthwise 1/4 position of the hot-rolled steel sheet during the cooling process of quenching is 5 ℃/sec or less, and the difference between the average cooling rate at the widthwise central position and the average cooling rate at the widthwise 3/4 position thereof is 5 ℃/sec or less.
6. The method for producing a wear-resistant steel sheet according to claim 5, wherein the cooling stop temperature in the quenching is lower than (Mf point-100 ℃),
after the quenching, the quenched hot-rolled steel sheet is tempered at a tempering temperature of (Mf point-80 ℃) to (Mf point +50 ℃).
7. The method for producing a wear-resistant steel sheet according to claim 6, wherein the tempering is performed while the steel sheet is maintained at the tempering temperature for 60 seconds or longer.
8. The method for producing a wear-resistant steel sheet according to claim 6 or 7, wherein the average temperature increase rate in the tempering is 2 ℃/sec or more.
9. The method for producing a wear-resistant steel sheet according to claim 5, wherein the cooling stop temperature during quenching is not higher than the Mf point and not lower than (Mf point-100 ℃) and not lower than,
after the quenching, the quenched hot-rolled steel sheet is air-cooled.
10. The method for producing a wear-resistant steel sheet according to any one of claims 5 to 9, wherein the composition further contains, in mass%, a component selected from the group consisting of Nb:0.005 to 0.020%, ti: 0.005-0.020% and B: 0.0003-0.0030% of the total amount of 1 or more than 2.
11. The method for producing a wear-resistant steel sheet according to any one of claims 5 to 10, wherein the composition further contains, in mass%, a component selected from the group consisting of Cu:0.01 to 0.5%, ni:0.01 to 3.0%, mo:0.1 to 1.0%, V:0.01 to 0.10%, W:0.01 to 0.5% and Co: 0.01-0.5% of 1 or more than 2.
12. The method for producing a wear-resistant steel sheet according to any one of claims 5 to 11, wherein the composition further contains, in mass%, a component selected from the group consisting of Ca:0.0005 to 0.0050%, mg:0.0005 to 0.0100% and REM: 0.0005-0.0200% of 1 or more than 2.
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