CN101688283A - Abrasion-resistant steel sheet having excellent processability, and method for production thereof - Google Patents

Abrasion-resistant steel sheet having excellent processability, and method for production thereof Download PDF

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CN101688283A
CN101688283A CN200880016192A CN200880016192A CN101688283A CN 101688283 A CN101688283 A CN 101688283A CN 200880016192 A CN200880016192 A CN 200880016192A CN 200880016192 A CN200880016192 A CN 200880016192A CN 101688283 A CN101688283 A CN 101688283A
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wear
steel plate
test
resisting steel
phase
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CN101688283B (en
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室田康宏
石川操
渡边好纪
铃木伸一
鹿内伸夫
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JFE Steel Corp
JFE Engineering Corp
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NKK Corp
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/06—Surface hardening
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite

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  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

An abrasion resistant steel excellent in bending formability and suitable for members, e.g., power shovels, which come into contact with earth and sand, and a production method thereof are provided. Specifically, the steel contains, on a percent by mass basis, 0.05% to 0.35% of C, 0.05% to 1.0% of Si, 0.1% to 2.0% of Mn, 0.1% to 1.2% of Ti, 0.1% or less of Al, at least one element of 0.1% to 1.0%of Cu, 0.1% to 2.0% of Ni, 0.1% to 1.0% of Cr, 0.05% to 1.0% of Mo, 0.05% to 1.0% of W, and 0.0003% to 0.0030% of B, if necessary at least one element of 0.005% to 1.0% of Nb and 0.005% to 1.0% of V,and the remainder including Fe and incidental impurities, where DI* represented by the following formula is less than 60. DI * = 33.85 0.1 C * 0.5 0.7 Si + 1 3.33 Mn + 1 0.35 Cu + 1 0.36 Ni + 1 2.16 Cr + 1 3 Mo * + 1 1.5 W * + 1 where C* = C - 1/4 (Ti - 48/14N), Mo* =; Mo (1 - 0.5 (Ti - 48/14N)), and W* = W (1 - 0.5 (Ti - 48/14N)).

Description

The wear-resisting steel plate of excellent processability and manufacture method thereof
Technical field
The present invention relates to wear-resisting steel plate (abrasion resistant steel) and manufacture method thereof, particularly relate to the good wear-resisting steel plate of bendability (bending formability), described wear-resisting steel plate is suitable as is building (construction), civil engineering work (civil engineering), use in the fields such as (mining), mine, power shovel (power shovels) for example, dozer (bulldozers), loading hopper (hoppers), scraper bowl industrial machineries (industrial machine) such as (buckets), transfer rollers (transporting machine) etc. contact with native sand (earth and sand) and the abrasion (wearor abrasion) that produce become the parts of problem and use.
Background technology
Be subjected to the abrasive parts of soil, sand etc., use the good steel of wear resistant for long lifetime.The wear resistant of known steel (abrasion resistant property) improves by high rigidityization, thereby require the parts of wear resistant, used heavy addition the steel of alloying elements such as Cr, Mo to implement thermal treatment such as quenching and the steel of high rigidityization.
For example, disclose in the Japanese kokai publication sho 62-142726 communique, will contain C:0.10～0.19%, contain an amount of Si, Mn, qualification C EqAfter 0.35～0.44% steel hot rolling, direct quenching is perhaps quenched behind reheat to 900～950 ℃, and 300～500 ℃ of annealing down, making surface of steel plate hardness is the manufacture method of the above wear-resisting steel plate of 300HV (vickers hardness).
Japanese kokai publication sho 63-169359 communique discloses, to containing C:0.10～0.20%, be adjusted to Si, Mn, P, S, N, Al an amount of or also contain the steel more than a kind of Cu, Ni, Cr, Mo, B, direct quenching after hot rolling, perhaps rolling, put cold back reheat and quench, give the manufacture method of the wear-resisting Plate Steel of the above hardness of its 340HB (Brinell hardness).
Japanese kokai publication hei 1-142023 communique discloses, to containing C:0.07～0.17%, be adjusted to Si, Mn, P, S, N, Al an amount of or also contain the steel more than a kind of Cu, Ni, Cr, Mo, B, direct quenching after hot rolling, or temporary transient air cooling to room temperature, reheat quenches, making it become surface hardness is that 321HB is above, the manufacture method of the wear-resisting steel plate of the steel plate of has excellent bending properties.
The technology of putting down in writing in Japanese kokai publication sho 62-142726 communique, Japanese kokai publication sho 63-169359 communique and the Japanese kokai publication hei 1-142023 communique, by adding alloying element in large quantities, effectively utilize solution hardening (solid solution hardening), transformation hardening (transformationhardening), precipitation-hardening (precipitation hardening) etc., carry out high rigidityization, the abrasion performance characteristic is improved.But, for adding alloying element in large quantities, effectively utilize solution hardening, transformation hardening, precipitation-hardening etc., carry out the situation of high rigidityization, weldability (weldability), processibility (formability) reduce, and manufacturing cost improves.
But, under the situation of the parts of requirement wear resistant, according to working conditions, exist and only make surface and near surface high rigidityization, promptly only make wear resistant improve situation about getting final product, thinking does not need to add in large quantities alloying elements such as Cr, Mo by the steel that are used for this situation, implement thermal treatments such as quench treatment, only make surface and near surface become quenching structure (hardened structure).
But, high rigidityization for quenching structure, usually, the solid solution C amount of steel is increased, but the increase of solid solution C amount, cause the reduction of weldability, the reduction of bendability etc., the particularly reduction of bendability make as the necessary bending machining of parts be restricted, working conditions is restricted.
Therefore, need not exceedingly to realize high rigidityization, and the wear-resisting steel plate that expectation can make the abrasion performance characteristic improve, disclose in No. 3089882 communiques of patent, contain C:0.10～0.45%, Si, Mn, P, S, N are adjusted in right amount, also contain Ti:0.1～1.0%, contain 400/mm 2TiC precipitate that above median size 0.5 μ m is above or the compound precipitate of TiC and TiN, TiS, Ti *Be more than 0.05% and less than the good wear resisting steel of 0.4% surface texture.
And, disclose in the Japanese kokai publication hei 4-41616 communique, by containing C:0.05～0.45%, Si:0.1～1.0%, Mn:0.1～1.0%, Ti:0.05～1.5%, and make surface hardness in Brinell hardness (Brinell hardness) below 401, make the manufacture method of the wear-resisting steel plate that bendability improves.
Technology according to the record of No. 3089882 communiques of Japanese Patent, Japanese kokai publication hei 4-41616 communique can generate with thick TiC the precipitate as main body when solidifying, thus not exceedingly high rigidityization, make the wear resistant raising at an easy rate.
But, the technology of No. 3089882 communique records of Japanese Patent, owing to implement quenching heat treatment, make tissue become the martensitic stucture (martensitic structure) of as-quenched condition, therefore intensity improves, its result, and the resistance to deformation (deformation resistance) during owing to bending machining improves, therefore it is easy to be difficult to bending machining, has problems on the bendability.
The technology of Japanese kokai publication hei 4-41616 communique record, in order to ensure bendability, with Brinell tester regulation surface hardness is below 401, but because the addition of alloying element is many, therefore tensile strength surpasses 780MPa, from making the viewpoint of the load reduction that adds man-hour, not necessarily realize sufficient bendability.
And, the wear-resisting steel plate of any record all must be implemented thermal treatment in Japanese kokai publication sho 62-142726 communique, Japanese kokai publication sho 63-169359 communique, Japanese kokai publication hei 1-142023 communique, the Japanese kokai publication hei 4-41616 communique, existing problems aspect manufacturing schedule, manufacturing cost (production cost).
Therefore, the objective of the invention is to, can be provided under the hot rolled state, do not implement thermal treatment and make, and the wear-resisting steel plate of wear resistant and has excellent bending properties and manufacture method thereof.
Summary of the invention
The inventor for achieving the above object, the various principal elements that influence wear resistant and bendability have been carried out research repeatedly, find, by having the composition system of containing Ti and C, make metal structure (microstructure of base metal) for the complex tissue (complex structure) of the ferrite-pearlite tissue of rolling state (ferrite and pearlite structure) as matrix phase (base phase), and second phase (second phase) (hard phase (hard phase): Ti is a carbide) of hard is dispersed in the matrix (matrix), can guarantee under the state of wear resistant thus, processing load when reducing bending machining promptly can be improved bendability.
The present invention is based on resulting opinion, further discusses and finishes, that is, the present invention is:
1. the wear-resisting steel plate of an excellent processability, it is characterized in that, in quality %, contain: C:0.05～0.35%, Si:0.05～1.0%, Mn:0.1～2.0%, Ti:0.1～1.2%, below the Al:0.1%, also contain in Cu:0.1～1.0%, Ni:0.1～2.0%, Cr:0.1～1.0%, Mo:0.05～1.0%, W:0.05～1.0%, B:0.0003～0.0030% more than a kind or 2 kinds, and the DI that represents by (1) formula *Less than 60, surplus is made of Fe and unavoidable impurities,
DI *＝33.85×(0.1×C *) 0.5×(0.7×Si+1)×(3.33×Mn+1)×(0.35×Cu+1)×(0.36×Ni+1)×(2.16×Cr+1)×(3×Mo *+1)×(1.5×W *+1)……(1)
Wherein, C *=C-1/4 * (Ti-48/14N), Mo *=Mo * (1-0.5 * (Ti-48/14N)), W *=W * (1-0.5 * (Ti-48/14N)), C, Si, Mn, Cu, Ni, Cr, Mo, W, Ti, N are content (quality %).
2. as 1 described wear-resisting steel plate, it is characterized in that,, also contain a kind or 2 kinds in Nb:0.005～1.0%, V:0.005～1.0% in quality %.
3. as 1 or 2 described wear-resisting steel plates, it is characterized in that as the matrix phase, and described matrix is dispersed with the hard phase in mutually to metal structure with ferrite-pearlite.
4. as 3 described wear-resisting steel plates, it is characterized in that the branch bulk density of described hard phase is 400/mm 2More than.
5. the manufacture method of the wear-resisting steel plate of an excellent processability is characterized in that, after the steel disc that will have 1 or 2 described compositions carried out hot rolling, the speed of cooling following with 2 ℃/s was cooled to below 400 ℃.
6. as the manufacture method of the wear-resisting steel plate of 5 described excellent processabilities, it is characterized in that the rolling rate when further making in the hot rolling below 920 ℃ is more than 30%, and to make rolling end temp be below 900 ℃.
And,, preferably make above-mentioned hard here mutually for Ti such as TiC is a carbide, TiC, (NbTi) C, (VTi) C can example be shown or in TiC solid solution the material of Mo, W.
According to the present invention, can be after hot rolling, do not implement thermal treatment and do not made the wear resistant variation, improved the wear-resisting steel plate of bendability, thereby can realize reducing thermal treatment cost and shortening manufacturing schedule etc. and reasonably produce, and on industry, given play to significant effect.
Description of drawings
Fig. 1 is the figure of expression Ti addition to the influence of wear resistant.
Fig. 2 is that expression Ti addition is to tensile properties (yield strength (yield strength): YS, tensile strength (tensile strength): the figure of influence TS).
Fig. 3 is expression DI *Figure to the influence of wear resistant.
Fig. 4 is expression DI *To tensile properties (yield strength: YS, tensile strength: the figure of influence TS).
Embodiment
Reason to wear-resisting steel plate predetermined component composition of the present invention, metal structure describes.
The % that (one-tenth is grouped into) is following is quality %.
C：0.05～0.35％
C makes the hardness of matrix improve, make wear resistant to improve in metal structure, and forming the Ti carbide of second phase as hard (below, be also referred to as the hard phase), is being effective elements improving aspect the wear resistant, in order to obtain such effect, need make its content is more than 0.05%.
On the other hand, the content of C surpasses at 0.35% o'clock, becomes thick as the carbide of hard phase, and producing with the carbide when bending machining is the crackle of starting point.Therefore, C is defined in 0.05～0.35% the scope.And, be preferably 0.15～0.32%.
Ti：0.1～1.2％
Ti and C are important element of the present invention, are the necessary elements that forms as the Ti carbide of the hard phase that helps to improve wear resistant.In order to obtain such effect, need make its content is more than 0.1%.
Fig. 1 represents the influence of Ti addition to wear resistant, and Fig. 2 represents that the Ti addition is to tensile properties (yield strength: YS, tensile strength: influence TS).Among Fig. 1, the longitudinal axis is represented abrasion performance ratio that the wear loss in the rubber wheel wear test (rubber wheel abrasion test) is compared with mild steel (mildsteel) abrasion loss (abrasion weight loss) (SS400).
The Ti addition is 0.1% when above, can obtain wear resistant and the common above characteristic of wear resisting steel par, and TS is reduced to below the 800MPa.That is, can have with carrying out the identical wear characteristic of wear-resisting steel plate of quenching heat treatment, and can improve processibility in the past.
The rubber wheel wear test for the examination steel, be after the steel disc that will contain 0.33%C-0.35%Si-0.82%Mn-0.05～1.2%Ti in quality % is rolling to 19mmt, carries out air cooling with the speed of cooling of 0.5 ℃/s and make.
The steel plate that obtains is implemented tension test and wear test.Tension test is gathered the JIS5 test film and is implemented tension test according to the regulation of JISZ2201, obtains tensile properties (tensile strength: TS, yield strength: YS).
Wear test is implemented by the rubber wheel wear test according to ASTM G65, recently puts the wear loss of mild steel (SS400) and each in order test-results for likening to abrasion performance of the wear loss of examination steel plate.Abrasion performance is bigger than more, and the expression wear characteristic is good more.
Test to the wear-resisting steel plate of making by common thermal treatment, is implemented test same as described above as a comparison.The result who obtains is shown in Fig. 1 and Fig. 2 as existing steel.Here, common wear-resisting steel plate is meant, behind the hot-rolled steel plate with the composition of 0.15 quality %C-0.35 quality %Si-1.50 quality %Mn-0.13 quality %Cr-0.13 quality %Mo-0.01 quality %Ti-0.0010 quality %B, behind the reheat to 900 ℃, implement the material of quenching heat treatment, be about the steel plate of 400HB with Brinell tester.
On the other hand, the content of Ti surpasses at 1.2% o'clock, thickization of hard phase (Ti is a carbide), and producing with thick hard during bending machining is the crackle of starting point mutually.Therefore, Ti is limited to 0.1～1.2%, preferably is limited in 0.1～0.8% the scope.
Si：0.05～1.0％
Si is an effective elements as deoxidant element (deoxidizing element), and in order to obtain such effect, need make its content is more than 0.05%.And, though Si is solid-solubilized in the steel, and help the effective elements of high rigidityization by solution strengthening, content was above 1.0% o'clock, ductility (ductility), toughness (toughness) are reduced, and produce problem such as inclusion amount (inclusioncontent) increase.Therefore, preferably Si is limited in 0.05～1.0% the scope.And, more preferably 0.05～0.40%.
Mn：0.1～2.0％
Mn is the effective elements that helps high rigidityization by solution strengthening, and in order to obtain such effect, need make its content is more than 0.1%.On the other hand, content surpasses at 2.0% o'clock, and weldability is reduced.Therefore, preferably Mn is limited in 0.1～2.0% the scope.And, more preferably 0.1～1.60%.
Below the Al:0.1%
Al plays a role as deoxidant element (deoxidizing element), and in order to obtain such effect, can make its content is more than 0.0020%, but contains in a large number and surpass at 0.1% o'clock, and the degree of cleaning (cleanness) of steel are reduced.Therefore, preferably Al is limited to below 0.1%.
In Cu:0.1～1.0%, Ni:0.1～2.0%, Cr:0.1～1.0%, Mo:0.05～1.0%, W:0.05～1.0%, B:0.0003～0.0030% more than a kind or 2 kinds
Cu：0.1～1.0％
Cu is the element that hardening capacity (hardenability) is improved by solid solution, and in order to obtain this effect, need make its content is more than 0.1%.On the other hand, content surpasses at 1.0% o'clock, and hot workability is reduced.Therefore, preferably Cu is limited in 0.1～1.0% the scope.And, more preferably 0.1～0.5%.
Ni：0.1～2.0％
Ni is the element that hardening capacity is improved by solid solution, and its content is that 0.1% this effect when above becomes remarkable.On the other hand, content surpasses at 2.0% o'clock, and material cost is significantly risen.Therefore, preferably Ni is limited in 0.1～2.0% the scope.And, more preferably 0.1～1.0%.
Cr：0.1～1.0％
Cr has the effect that the hardening capacity of making improves, and in order to obtain such effect, need make its content is more than 0.1%, but content surpasses at 1.0% o'clock, and weldability is reduced.Therefore, preferably Cr is limited in 0.1～1.0% the scope.And, more preferably 0.1～0.8%.More preferably 0.4～0.7%.
Mo：0.05～1.0％
Mo is the element that hardening capacity is improved.In order to obtain such effect, need make its content is more than 0.05%.On the other hand, if content surpasses 1.0%, weldability is reduced.Therefore, preferably Mo is limited in 0.05～1.0% the scope.And, more preferably 0.05～0.40%.
W：0.05～1.0％
W is the element that hardening capacity is improved.In order to obtain such effect, need make its content is more than 0.05%.On the other hand, if content surpasses 1.0%, weldability is reduced.Therefore, preferably W is limited in 0.05～1.0% the scope.And, more preferably 0.05～0.40%.And, because Mo, W are solid-solubilized among the TiC, therefore also have the effect of the amount increase that makes the hard phase.
B：0.0003～0.0030％
B is segregation in crystal boundary (grain boundary), strengthens crystal boundary, helps to improve the flexible element effectively, and in order to obtain such effect, need make its content is more than 0.0003%.On the other hand, content surpasses at 0.0030% o'clock, and weldability is reduced.Therefore, preferably B is limited in 0.0003～0.0030% the scope.And, more preferably 0.0003～0.0015%.
DI *＜60
Among the present invention, DI *(hardening capacity desired value (hardenability index)) is with DI *=33.85 * (0.1 * C *) 0.5* (0.7 * Si+1) * (3.33 * Mn+1) * (0.35 * Cu+1) * (0.36 * Ni+1) * (2.16 * Cr+1) * (3 * Mo *+ 1) * (1.5 * W *+ 1), C wherein *=C-1/4 * (Ti-48/14N), Mo *=Mo * (1-0.5 * (Ti-48/14N)), W *=W * (1-0.5 * (Ti-48/14N)) define, make DI *＜60.Here, C, Si, Mn, Cu, Ni, Cr, Mo, W, Ti, N are content (quality %).Represent DI among Fig. 3 *To the influence of wear resistant, represent DI among Fig. 4 *To tensile properties (yield strength: YS, tensile strength: influence TS).Among Fig. 3, the longitudinal axis is represented abrasion performance ratio that the wear loss in the rubber wheel wear test is compared with the wear loss of mild steel (SS400).Abrasion performance is bigger than more, and the expression wear characteristic is good more.
According to Fig. 3 and Fig. 4 as can be known, DI *Less than 60 o'clock, even tensile strength: TS is the following low strength of 800MPa, and wear loss is a par with common wear resisting steel also.
On the other hand, if DI *Be more than 60, though then abradability is good, tensile strength is poor in processability when 800MPa is above.Infer that its reason is DI *Be 60 when above, become ferrite-bainite structure (ferrite and bainite structure).
The rubber wheel wear test for the examination steel, be with contain in quality % 0.34%C-0.22%Si-0.55%Mn-0.22%Ti, also contain Cu, Ni, Cr, Mo, W more than a kind or 2 kinds and DI *Be after 40～120 steel disc is rolling to 8mmt, carry out air cooling (speed of cooling: 1.2 ℃/s) make.
To the steel plate that obtains, implement tension test and wear test.Tension test is gathered the JIS5 test film and is implemented tension test according to the regulation of JISZ2201, obtains tensile properties (tensile strength TS, yield strength YS).
The rubber wheel wear test is implemented according to ASTMG65, and test-results is by recently putting likening to abrasion performance of the wear loss of the wear loss of mild steel (SS400) and each steel plate in order.
By mentioned component is basal component, can obtain good wear resistant, but in the present invention, further improves in order to make wear resistant, can contain second phase that forms hard, the element nb that helps wear resistant, V as selecting element.
Nb：0.005～1.0％
The compound interpolation of Nb and Ti forms the double carbide ((NbTi) C) of Ti, Nb thus, disperses mutually as second of hard, and be the element that helps to improve wear resistant effectively.In order to obtain the effect of such raising wear resistant, need make its content is more than 0.005%.On the other hand, content surpasses at 1.0% o'clock, thickization of second phase of hard (double carbide of Ti, Nb), and second phase (double carbide of Ti, Nb) that produces with hard during bending machining is the crackle of starting point.Therefore, during interpolation, preferably Nb is limited in 0.005～1.0% the scope.And, more preferably 0.1～0.5%.
V：0.005～1.0％
The compound interpolation of V and Ti similarly forms the double carbide ((VTi) C) of Ti, V thus with Nb, disperses mutually as second of hard, and be the element that helps to improve wear resistant effectively.In order to obtain the effect of such raising wear resistant, need make its content is more than 0.005%.
On the other hand, content surpasses at 1.0% o'clock, thickization of second phase of hard (double carbide of Ti, V), and second phase (double carbide of Ti, V) that produces with hard during bending machining is the crackle of starting point.Therefore, during interpolation, preferably V is limited in 0.005～1.0% the scope.And, more preferably 0.1～0.5%.
And for the situation with Nb and the compound interpolation of V, second of hard becomes (NbVTi) C mutually, only similarly has the effect that wear resistant is improved thus.And, for the situation that contains N, except that carbide, form the situation of carbonitride in addition, can obtain same effect.
But, surpassing 0.01% situation for the N addition, the ratio of the N in the carbonitride increases, and the hardness of hard second phase reduces, and wear resistant might variation.Therefore, preferably make the N addition below 0.01%.
(metal structure)
Wear-resisting steel plate of the present invention, metal structure is for being dispersed with the tissue of hard phase (hard second phase) in mutually as matrix phase and this matrix with ferrite-pearlite.Matrix is meant the volume fraction that has more than 90% mutually, steel plate of the present invention, and ferrite and perlite two-phase account for more than 90% of integral body.
And wherein, the volume fraction of preferred ferritic phase is more than 70%, and to justify the ferritic phase of equivalent diameter median size 20 μ m.Consider processibility, preferred substrate is counted below the 300HB with Brinell hardness.
As the hard phase, Ti such as preferred TiC are carbide, can illustration TiC, (NbTi) C, (VTi) C or in TiC solid solution the material of Mo, W.
In addition, the size of hard phase is not particularly limited, but from the viewpoint of wear resistant, be preferably about 0.5 μ m above, below about 50 μ m.And the branch bulk density of hard phase from the viewpoint of wear resistant, is preferably 400/mm 2More than.
In addition, big or small following the obtaining of hard phase: measure the area of each hard phase, calculate round equivalent diameter by equal area, the resulting round equivalent diameter of arithmetical mean is with the size (median size) of mean value as the hard phase of this steel plate.
(manufacture method)
Wear-resisting steel plate of the present invention is preferably used the molten steel of the above-mentioned composition of known melting method melting, by Continuous casting process or ingot casting-split rolling method method (ingot making-blooming method), obtains the steel billet former materials of steel such as (slab) of predetermined size.
For hard is adjusted to predetermined size and number mutually, for example, when adopting Continuous casting process, the preferred adjustment cooled off, so that the speed of cooling of casting sheet in 1500～1200 ℃ temperature range of thick 200～400mm reaches the scope of 0.2～10 ℃/s.
In addition, for the situation that adopts ingot casting method, need to adjust the size and the cooling conditions of ingot (ingot) certainly, so that hard becomes desired size and number mutually.
Then, do not cool off the former material of steel, after hot rolling immediately or the cooling, after reheat to 950～1250 ℃, hot rolling obtains the steel plate of desired thickness of slab.After the hot rolling, do not heat-treat, with the following average cooling rate cooling of 2 ℃/s.
If speed of cooling greater than 2 ℃/s, then can not obtain the ferrite-pearlite tissue, tensile strength reaches more than the 800MPa, and the processing load that steel plate bending adds man-hour rises the processibility variation.Therefore, make speed of cooling be 2 ℃/below the s.
In addition, hot-rolled condition is not particularly limited, as long as can make the steel plate of desired size shape, but if be considered as the toughness of the performance that steel plate should have, then needing to make the surface temperature of steel plate, the rolling rate below 920 ℃ is more than 30%, and to make rolling end temp be below 900 ℃.
Wear-resisting steel plate of the present invention need not implemented thermal treatment after hot rolling, can be used in the various uses that needs bending machining under the hot-rolled state.
Embodiment
The molten steel of forming shown in the table 1 is carried out melting in vacuum melting furnace, form small-sized steel ingot (50kg) (the former material of steel) after, be heated to 1050～1250 ℃ and implement hot rolling, make its become thickness of slab 6～100mm for the examination steel plate.Each is implemented structure observation, tension test (tensiletest), wear test, Charpy impact test (Charpy impact test), pliability test (bend test) for the examination steel plate.
(structure observation)
After structure observation ground with test film, corrode with nitric acid ethanol (nital), position to 1mm under the top layer, use opticmicroscope (optical microscope) (multiplying power (magnificationratio): 400 times), appraisement organization, and size, the number of mensuration ferrite particle diameter (ferrite grain diameter) and hard phase.In addition, in field of view, to account for tissue more than 90% as the matrix phase, the median size of the size of hard phase for trying to achieve by preceding method.
(tension test)
According to the regulation of JIS Z2201, gather No. 5 test films of JIS, implement tension test according to the regulation of JIS Z2241, obtain tensile properties (yield strength: YS, tensile strength: TS).Tensile strength (TS)＜800MPa, yield strength (YS)＜600MPa are made as the scope of the invention.
(wear test)
Making test film is t (thickness of slab) * 20 * 75 (mm), according to the regulation of ASTM G 65, uses abrasive sand (abrasive sand) to implement the rubber wheel wear test.After the test, the wear loss of determination test sheet.
Test-results, is estimated with abrasion performance ratio=(wear loss of mild steel plate)/(wear loss of each steel plate) as standard (1.0) with the wear loss of mild steel (SS400) plate.Abrasion performance is better more than big more expression wear resistant, and the scope of the invention is made as the abrasion performance ratio: more than 4.0.
(Charpy impact test)
Regulation according to JIS Z2202, begin to gather V test with notched test piece sheet from the position of thickness of slab direction 1/4 along the L direction, according to the regulation of JIS Z2242, implement Charpy impact test down for 0 ℃ in test temperature, obtain the summer than absorbing energy (Charpy absorbed energy).The test radical is made as 3, obtains mean value.
(pliability test)
According to the regulation of JIS Z2204, wide be under the situation more than the 45mm for 50mm, for the thickness of slab of examination steel plate, grind from the single face side, gather the test film that thickness of slab reduces to 25mm; Under the situation of thickness of slab less than 45mm for the examination steel plate, gather the test film of this thickness of slab, according to the regulation of JIS Z2248, implement pliability test.Pliability test is that r=1.5t implements by the method for buckling with the bending radius.
The table 2 that the results are shown in structure observation, tension test, wear test.Example of the present invention (steel plate No.1～6, steel plate No.8,9) is although tensile strength (TS)＜800MPa, yield strength (YS)＜600MPa is the very good steel plate of wear resistant.
And the summer can be to be more than the 27J below 900 ℃ the time in finishing temperature than absorbing.On the other hand, it is poor that comparative example and example of the present invention are compared wear resistant, even perhaps wear resistant is suitable, but because YS, TS height, so bendability is poor.
Table 1
Steel Mark ??C ??Si ??Mn ??P ??S ??Cu ??Ni ??Cr ??Mo ??W ??V ??Nb ??Ti ??B ??Al ??N ??DI * Remarks
??A ??0.12 ??0.33 ??1.22 ??0.015 ??0.003 ??- ??- ??0.81 ??0.12 ??- ??- ??- ??0.28 ??0.0011 ??0.025 ??0.0025 ??54.9 Example
??B ??0.15 ??0.41 ??1.06 ??0.014 ??0.005 ??- ??- ??0.25 ??0.35 ??0.22 ??- ??- ??0.46 ??0.0013 ??0.035 ??0.0031 ??42.5 Example
??C ??0.25 ??0.27 ??1.12 ??0.012 ??0.008 ??0.45 ??0.35 ??- ??0.24 ??0.33 ??- ??- ??0.67 ??- ??0.051 ??0.0029 ??45.1 Example
??D ??0.30 ??0.43 ??1.31 ??0.008 ??0.011 ??- ??- ??- ??0.33 ??- ??- ??- ??0.74 ??0.0018 ??0.045 ??0.0045 ??42.0 Example
??E ??0.35 ??0.44 ??1.15 ??0.013 ??0.012 ??- ??- ??0.45 ??0.25 ??0.35 ??- ??- ??0.98 ??0.0006 ??0.038 ??0.0046 ??77.7 Example
??F ??0.25 ??0.29 ??0.88 ??0.011 ??0.004 ??- ??- ??0.28 ??0.12 ??- ??0.05 ??- ??0.77 ??- ??0.051 ??0.0029 ??55.2 Example
??G ??0.25 ??0.23 ??0.83 ??0.015 ??0.003 ??- ??- ??0.33 ??0.15 ??- ??- ??0.31 ??0.63 ??0.0025 ??0.051 ??0.0029 ??58.1 Example
??H ??0.25 ??0.15 ??0.55 ??0.013 ??0.002 ??- ??- ??0.45 ??0.24 ??- ??0.02 ??0.02 ??0.59 ??- ??0.051 ??0.0029 ??56.8 Example
??I ??0.28 ??0.33 ??0.78 ??0.012 ??0.004 ??- ??- ??0.34 ??0.11 ??- ??- ??- ??0.01 * ??0.0022 ??0.038 ??0.0033 ??57.9 Comparative example
??J ??0.24 ??0.29 ??1.18 ??0.013 ??0.005 ??- ??- ??0.57 ??0.22 ??- ??- ??- ??0.9 ??0.0017 ??0.044 ??0.0034 ??115.2 * Comparative example
??K ??0.22 ??0.35 ??1.44 ??0.013 ??0.003 ??- ??- ??0.46 ??0.18 ??- ??- ??- ??0.01 * ??0.0001 ??0.048 ??0.0043 ??111.2 * Comparative example
??L ??0.31 ??0.36 ??0.71 ??1.02 ??0.23 ??0.045 ??0.38 ??0.0008 ??0.045 ??0.0033 ??105.3 * Comparative example
Annotate 1: *Outside the mark scope of the invention
Annotate 2:DI *=33.85 * (0.1 * C *) 0.5* (0.7 * Si+1) * (3.33 * Mn+1) * (0.35 * Cu+1) * (0.36 * Ni+1) * (2.16 * Cr+1) * (3 * Mo *+ 1) * (1.5 * W *+ 1)
Table 2
Figure A20088001619200181
Annotate 1: *Outside the mark scope of the invention
Annotate 2: abrasion performance is than (wear loss of mild steel plate)/(wear loss of each steel plate)
(scope of the invention: the abrasion performance ratio is more than 4.0)
Table 3
Figure A20088001619200191
Annotate 1: abrasion performance is than (wear loss of mild steel plate)/(wear loss of each steel plate)
(scope of the invention: the abrasion performance ratio is more than 4.0)
Annotate 2:vE 0(J): the summer under 0 ℃ of the test temperature, absorb can (J) than impacting

Claims (6)

1. wear-resisting steel plate, it is characterized in that, in quality %, contain: C:0.05～0.35%, Si:0.05～1.0%, Mn:0.1～2.0%, Ti:0.1～1.2%, below the Al:0.1%, also contain in Cu:0.1～1.0%, Ni:0.1～2.0%, Cr:0.1～1.0%, Mo:0.05～1.0%, W:0.05～1.0%, B:0.0003～0.0030% more than a kind or 2 kinds, and the DI that represents by (1) formula *Less than 60, surplus is made of Fe and unavoidable impurities,
DI *＝33.85×(0.1×C *) 0.5×(0.7×Si+1)×(3.33×Mn+1)×(0.35×Cu+1)×(0.36×Ni+1)×(2.16×Cr+1)×(3×Mo *+1)×(1.5×W *+1)……(1)
Wherein, C *=C-1/4 * (Ti-48/14N), Mo *=Mo * (1-0.5 * (Ti-48/14N)), W *=W * (1-0.5 * (Ti-48/14N)), here, C, Si, Mn, Cu, Ni, Cr, Mo, W, Ti, N are quality % content.
2. wear-resisting steel plate as claimed in claim 1 in quality %, also contains a kind or 2 kinds in Nb:0.005～1.0%, V:0.005～1.0%.
3. as the matrix phase, and described matrix is dispersed with the hard phase in mutually with ferrite-pearlite for wear-resisting steel plate as claimed in claim 1 or 2, metal structure.
4. wear-resisting steel plate as claimed in claim 3, the branch bulk density of described hard phase is 400/mm 2More than.
5. the manufacture method of a wear-resisting steel plate, after the steel disc that will have claim 1 or 2 described compositions carried out hot rolling, the speed of cooling following with 2 ℃/s was cooled to below 400 ℃.
6. the manufacture method of the wear-resisting steel plate of excellent processability as claimed in claim 5, wherein, the rolling rate when further making in the hot rolling below 920 ℃ is more than 30%, and to make rolling end temp be below 900 ℃.
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