CN104685088A - Wear-resistant steel plate having excellent low-temperature toughness and corrosion wear resistance - Google Patents

Wear-resistant steel plate having excellent low-temperature toughness and corrosion wear resistance Download PDF

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Publication number
CN104685088A
CN104685088A CN201380048598.5A CN201380048598A CN104685088A CN 104685088 A CN104685088 A CN 104685088A CN 201380048598 A CN201380048598 A CN 201380048598A CN 104685088 A CN104685088 A CN 104685088A
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steel plate
wear
content
resistant steel
corrosion
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三浦进一
植田圭治
石川信行
高山直树
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JFE Steel Corp
JFE Engineering Corp
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NKK Corp
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Abstract

Provided is a wear-resistant steel plate having excellent wear resistance, low-temperature toughness, and corrosion wear-resistance. The wear-resistant steel plate is characterized in: containing, in terms of mass percent, 0.23-0.35% C, 0.05-1.00% Si, 0.1-2.0% Mn, no more than 0.020% P, no more than 0.005% S, 0.005-0.100% Al, 0.03-2.0% Cr, and 0.03-1.0% Mo, so as to satisfy the condition that DI* defined in formula (1) below is at least 45; having a component structure comprising a remainder of Fe and unavoidable impurities; using an as-quenched martensite phase as a main phase; having a structure in which the prior austenite grain size is no larger than 30 mum; and having the surface hardness be at least 450 in terms of a Brinell hardness of HBW 10/3000.

Description

The wear-resistant steel plate of low-temperature flexibility and corrosion wear resistance excellence
Technical field
The present invention relates to the wear-resistant steel plate (abrasion resistant steel plate) of the parts being suitable for industrial machine, haulage equipment etc.Wear-resistant steel plate excellent in low temperature toughness of the present invention, the parts that the position being particularly suitable for becoming problem in the wearing and tearing produced because contacting with sand with the soil containing moisture uses.
Background technology
All the time, in building, building, mine etc. industrial machine, the haulage equipment etc. such as such as power shovel, dozer, hopper, well-bucket, wagon tremie that building site uses parts because of with soil and contacting of sand etc. and wear and tear.Therefore, when manufacturing above-mentioned parts, use the steel of excellent in wear resistance to extend its life-span.In view of the environment for use of reality, assuming that soil and sand etc. have drying, the various state such as moistening.Particularly be in the soil of moisture state and sand etc. sometimes containing corrosives (corrosive material).In this case, being in wearing and tearing that the soil of moisture state and sand etc. produce will become into containing the wearing and tearing under the environment of corrosives, i.e. so-called corrosive wear (corrosive wear).Known corrosive wear is very harsh as abrasion environment.Therefore, the wear-resistant steel of demand corrosion wear resistance excellence.
In addition, also suppose that the low temperature environment below 0 DEG C such as these industrial machine, haulage equipments etc. uses.Therefore, require that the steel used in the parts of these industrial machine, haulage equipments etc. also have excellent low-temperature flexibility on the basis with wearability, corrosion wear resistance.
For such requirement, such as, in patent documentation 1, propose a kind of manufacture method of high-hardness wear-resistant steel of excellent in low temperature toughness, that is, after carrying out hot rolling to the steel disc with following composition, from Ar 3temperature more than transformation temperature starts to carry out quench treatment, then tempering is carried out, obtain high intensity wear-resistant steel, above-mentioned steel disc is in mass % containing C:0.30 ~ 0.50%, and containing appropriate Si, Mn, Al, N, Ti, Nb, B, also containing Cr:0.10 ~ 0.50%, Mo:0.05 ~ 1.00%.In the technology that patent documentation 1 is recorded, by containing a large amount of Cr, Mo, improve the hardenability of steel, and enhance crystal boundary, improve low-temperature flexibility.In addition, in the technology that patent documentation 1 is recorded, further increase low-temperature flexibility by implementing temper.
In addition, in patent documentation 2, propose the high-toughness and wear-resistant steel plate of the toughness after a kind of shrend and temper and delayed fracture resistance characteristics excellence, it is in mass % containing C:0.18 ~ 0.25%, Si:0.10 ~ 0.30%, Mn:0.03 ~ 0.10%, and containing appropriate Nb, Al, N, B, also containing Cr:1.00 ~ 2.00%, Mo: more than 0.50 ~ 0.80%.In the technology that patent documentation 2 is recorded, by Mn content being suppressed to lower and containing a large amount of Cr, Mo, improve the hardenability of steel plate, the hardness specified can be guaranteed, and improve toughness and delayed fracture resistance characteristics.In addition, in the technology that patent documentation 2 is recorded, further increase low-temperature flexibility by implementing temper.
In addition, in patent documentation 3, propose a kind of high-toughness and wear-resistant steel, it is in mass % containing C:0.30 ~ 0.45%, Si:0.10 ~ 0.50%, Mn:0.30 ~ 1.20%, Cr:0.50 ~ 1.40%, Mo:0.15 ~ 0.55%, B:0.0005 ~ 0.0050%, sol.Al:0.015 ~ 0.060%, also containing appropriate Nb and/or Ti.In the technology that patent documentation 3 is recorded, by containing a large amount of Cr, Mo, improve the hardenability of steel, and enhance crystal boundary, improve low-temperature flexibility.
In addition, in patent documentation 4, propose a kind of manufacture method of Abrasion Resistant Steels, that is, to the steel with following composition with accumulation draft in the austenite Unhydrated cement of less than 900 DEG C be more than 50% carry out hot rolling after, from Ar 3starts quenching more than, carry out thereafter tempering, above-mentioned steel, in mass % containing C:0.05 ~ 0.40%, Cr:0.1 ~ 2.0%, also containing appropriate Si, Mn, Ti, B, Al, N, can contain Cu, Ni, Mo, V as any composition further.In this technology, direct quenching, tempering are carried out to the tissue that austenite crystal stretches, form the tempered martensite that original austenite grain crystalline substance is stretched, thus significantly improve low-temperature flexibility.
In addition, in patent documentation 5, propose a kind of wear-resistant steel plate with the excellent in low temperature toughness of following composition, it is in mass % containing C:0.10 ~ 0.30%, Si:0.05 ~ 1.0%, Mn:0.1 ~ 2.0%, W:0.10 ~ 1.40%, B:0.0003 ~ 0.0020%, also containing Ti:0.005 ~ 0.10% and/or Al:0.035 ~ 0.1%.Should illustrate, in the technology that patent documentation 5 is recorded, can further containing more than a kind that is selected from Cu, Ni, Cr, V.Thus, make steel plate have high surface hardness, excellent in wear resistance, and low-temperature flexibility is also excellent.
In addition, in patent documentation 6, describe the wear-resistant steel plate of excellent in bending workability.The technology that patent documentation 6 is recorded relates to and a kind ofly to have in mass % containing the composition that C:0.05 ~ 0.30%, Ti:0.1 ~ 1.2% and solid solution C amount are less than 0.03%, and has the wear-resistant steel plate that matrix is the tissue being dispersed with hard phase in ferritic phase, matrix.Should illustrate, the wear-resistant steel plate recorded in patent documentation 6 can further containing a kind or 2 kinds in Nb, V, a kind in Mo, W or 2 kinds, a kind in Si, Mn, Cu or 2 kinds, a kind in Ni, B or 2 kinds and Cr.Thus, in patent documentation 6 record wear-resistant steel plate make when the not obvious increase of its hardness for soil and sand wear and tear wearability and bendability all improve.
Prior art document
Patent documentation
Patent documentation 1: Japanese Unexamined Patent Publication 08-41535 publication
Patent documentation 2: Japanese Unexamined Patent Publication 02-179842 publication
Patent documentation 3: Japanese Laid-Open Patent Publication 61-166954 publication
Patent documentation 4: Japanese Unexamined Patent Publication 2002-20837 publication
Patent documentation 5: Japanese Unexamined Patent Publication 2007-92155 publication
Patent documentation 6: Japanese Unexamined Patent Publication 2007-197813 publication
Summary of the invention
The object of each technology recorded in patent documentation 1 ~ 5 is to possess low-temperature flexibility and wearability.In addition, the object of the technology recorded in patent documentation 6 is to have bendability and wearability concurrently.All research was not carried out to the wearing and tearing that contain the environment of corrosives under such at the soil and sand that are in moisture state in these patent documentations, there is the problem not having pay abundant attention corrosion wear resistance such.
In addition, to carry out tempering as prerequisite, there is manufacturing cost and increase such problem in each technology recorded in patent documentation 1 ~ 4.In addition, the technology recorded in patent documentation 5 must contain W, there is the problem that manufacturing cost increases.In addition, the technology recorded in patent documentation 6 is principal phase with ferrite, there is the low and insufficient such problem of wearability of surface hardness.
The object of the invention is to the problem solving above-mentioned prior art, provide excellent in wear resistance with cheap cost and the wear-resistant steel plate of combined with superior low-temperature flexibility and excellent corrosion wear resistance.
The present inventor etc. to achieve these goals, conduct in-depth research the wearability of steel plate and the impact of various important factor on low-temperature flexibility, corrosion wear resistance.Its result, the present inventor etc. find, by becoming containing the composition of the addition of C r and Mo as required composition, can significantly improve the corrosion wear resistance of steel plate.Infer this is because by containing Cr and Mo, even if in the steel plate soil that is exposed to the moisture state with various pH and sand, because Cr and Mo exists with the form of oxygen acid, so suppression corrosive wear.
In addition, if the present inventor etc. find on the basis becoming above-mentioned composition, can the surface hardness of steel plate be maintained higher, then for soil and sand wear and tear wearability and corrosion wear resistance significantly improve.
In addition, the present inventor etc. find by making steel plate contain the addition of C r and Mo as required composition, and be that the mode of more than 45 is at least containing the addition of C to meet the DI* defined by following formula (1), Si, Mn, P, S, Al, Cr, Mo, hardenability can be improved, by forming the tissue being principal phase with quenching state martensitic phase, can guarantee that surface hardness counts more than 450 with Brinell hardness HBW10/3000, additionally by being less than 30 μm by the miniaturization of quenching state martensitic phase to original austenite (γ) particle diameter, excellent wearability can be guaranteed, and excellent low-temperature flexibility can be guaranteed.
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)×(1.75×V+1) (1)
(wherein, C, Si, Mn, Cu, Ni, Cr, Mo, V: the content (quality %) of each element)
The present invention studies further based on above-mentioned viewpoint and completes.That is, main points of the present invention are as follows.
(1) the wear-resistant steel plate of a kind of low-temperature flexibility and corrosion wear resistance excellence, it is characterized in that, there is following one-tenth be grouped into: contain C:0.23 ~ 0.35% in mass % in the mode that the satisfied DI* defined by following formula (1) is more than 45, Si:0.05 ~ 1.00%, Mn:0.1 ~ 2.0%, below P:0.020%, below S:0.005%, Al:0.005 ~ 0.100%, Cr:0.03 ~ 2.0%, Mo:0.03 ~ 1.0%, remainder is made up of Fe and inevitable impurity, and have with quenching state martensitic phase for principal phase and original austenite particle diameter is the tissue of less than 30 μm, surface hardness counts more than 450 with Brinell hardness HBW10/3000.
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) × (1.75 × V+1) formula (1)
(C, Si, Mn, Cu, Ni, Cr, Mo and V in formula (1) are the content (quality %) of each element.)
(2) the wear-resistant steel plate Gen Ju (1), it is characterized in that, on the basis of mentioned component, one kind or two or more containing what be selected from Nb:0.005 ~ 0.1%, Ti:0.005 ~ 0.1% and V:0.005 ~ 0.1% in mass % further.
(3) the wear-resistant steel plate Gen Ju (1) or (2), is characterized in that, on the basis of mentioned component, further in mass % containing a kind that is selected from Sn:0.005 ~ 0.2% and Sb:0.005 ~ 0.2% or 2 kinds.
(4) according to the wear-resistant steel plate in (1) ~ (3) described in wantonly 1, it is characterized in that, on the basis of mentioned component, one kind or two or more containing what be selected from Cu:0.03 ~ 1.0%, Ni:0.03 ~ 2.0% and B:0.0003 ~ 0.0030% in mass % further.
(5) according to the wear-resistant steel plate in (1) ~ (4) described in wantonly 1, it is characterized in that, on the basis of mentioned component, one kind or two or more containing what be selected from REM:0.0005 ~ 0.008%, Ca:0.0005 ~ 0.005% and Mg:0.0005 ~ 0.005% in mass % further.
(6) according to the wear-resistant steel plate in (1) ~ (5) described in wantonly 1, it is characterized in that, the content of above-mentioned quenching state martensitic phase counts more than 98% with volume fraction.
According to the present invention, easily and stably can manufacture that corrosion wear resistance especially under the soil and sand abrasion environment of moisture state is excellent and low-temperature flexibility is also excellent and stably have the wear-resistant steel plate of excellent wearability when not reducing surface hardness.
Embodiment
First, the restriction reason of the composition of wear-resistant steel plate of the present invention (being sometimes referred to as in this specification sheets " steel plate ") is described.Should illustrate, below, when not having specified otherwise, quality % is simply designated as %.
C：0.23～0.35％
C increases the hardness of steel plate, the element of raising wearability.The content of C lower than 0.23% time can not get sufficient hardness.On the other hand, if the content of C is more than 0.35%, then the weldability of steel plate, low-temperature flexibility and processibility decline.Therefore, the content of C is limited to the scope of 0.23 ~ 0.35%.Should illustrate, the content of preferred C is 0.25 ~ 0.30%.
Si：0.05～1.00％
Si is the element played a role as the reductor of molten steel, in addition, is the element contributing to the intensity improving steel plate because of solution strengthening.In order to ensure such effect, the content of Si is set to more than 0.05%.The content of Si lower than 0.05% time fully cannot obtain deoxidation effect.On the other hand, if the content of Si is more than 1.00%, then the ductility of steel plate, toughness decline, and the inclusion amount in addition in steel plate increases.Therefore, the content of Si is limited to the scope of 0.05 ~ 1.00%.Should illustrate, the content of preferred Si is 0.15 ~ 0.45%.
Mn：0.1～2.0％
Mn is the element with the effect improving hardenability.In order to ensure such effect, the content of Mn is set to more than 0.1%.On the other hand, if the content of Mn is more than 2.0%, then produce temper brittleness, and welding heat affected zone is hardening, weldability declines.Therefore, the content of Mn is limited to the scope of 0.1 ~ 2.0%.Should illustrate, the content of preferred Mn is 0.4 ~ 1.7%, is more preferably 0.5 ~ 1.0%.
Below P:0.020%
If then cause the low-temperature flexibility of steel plate to decline a large amount of in steel containing P, therefore preferably the content of P is as far as possible few.The content of P can be allowed in the present invention to be less than 0.020%.Should illustrate, if excessively reduce the content of P, cause the surging of refining cost.Therefore, the content of P is preferably more than 0.005%.
Below S:0.005%
If a large amount of containing S in steel, then S separates out with the form of MnS.In high-strength steel, MnS becomes the starting point destroyed and occur, and causes the toughness deterioration of steel plate.Therefore, the content of preferred S is as far as possible few.As long as the content of S is less than 0.005% then can to allow in the present invention.Thus, the content of S is limited to less than 0.005%.Should illustrate, the content excessively reducing S causes the surging of refining cost.Therefore, the content of S is preferably more than 0.0005%.
Al：0.005～0.100％
Al is the element played a role as the reductor of molten steel.In addition, Al makes crystal grain miniaturization, contributes to improving low-temperature flexibility.In order to obtain such effect, the content of Al is set to more than 0.005%.The content of Al lower than 0.005% time cannot fully obtain these effects.On the other hand, if the content of Al is more than 0.100%, then the weldability of steel plate declines.Therefore, the content of Al is limited to the scope of 0.005 ~ 0.100%.Should illustrate, the content of preferred Al is 0.015 ~ 0.050%.
Cr：0.03～2.0％
Cr improves hardenability.In addition, Cr has and makes martensitic phase miniaturization and the effect improving low-temperature flexibility.Therefore, in the present invention, Cr is important element.In addition, with the soil of moisture state and sand etc. contact the corrosive wear environment becoming problem under, Cr with the form stripping of chromate ion by anodic reaction, is played inhibitor effect and suppresses corrosion, thus improving the corrosion wear resistance of steel plate.In order to obtain such effect, the content of Cr is set to more than 0.03%.The content of Cr lower than 0.03% time, such effect cannot be given full play to.On the other hand, if the content of Cr is more than 2.0%, then weldability declines, and manufacturing cost is surging.Therefore, the content of Cr is limited to the scope of 0.03 ~ 2.0%.Should illustrate, the content of preferred Cr is 0.07 ~ 1.0%, is more preferably the scope of 0.2 ~ 0.9%.
Mo：0.03～1.0％
Mo improves hardenability.In addition, Mo has and makes martensitic phase miniaturization and the effect improving low-temperature flexibility.In the present invention, Mo is important element.In addition, with the soil of moisture state and sand etc. contact the corrosive wear environment becoming problem under, Mo has by anodic reaction with the form stripping of molybdenum acid ion, plays inhibitor effect and suppresses corrosion, thus improving the effect of corrosion wear resistance.In order to obtain such effect, the content of Mo is set to more than 0.03%.The content of Mo lower than 0.03% time, such effect cannot be given full play to.On the other hand, if the content of Mo is more than 1.0%, then the weldability of steel plate declines, and manufacturing cost is surging.Therefore, the content of Mo is limited to the scope of 0.03 ~ 1.0%.Should illustrate, the content of preferred Mo is 0.10 ~ 0.50%, is more preferably 0.20 ~ 0.40%.
By making steel plate compound contain Cr and Mo, significantly improving of corrosion wear resistance can be expected.Infer that this is because Cr with Mo can be different with the pH region of oxygen acid form existence, the corrosive wear that the soil of the moisture state of the pH with wide region and sand etc. cause can be suppressed.
Above-mentioned composition is basal component.Wear-resistant steel plate of the present invention is on the basis containing above-mentioned basal component, selectivity can also contain and be selected from Nb:0.005 ~ 0.1%, Ti:0.005 ~ 0.1%, one kind or two or more in V:0.005 ~ 0.1% and/or be selected from Sn:0.005 ~ 0.2%, 1 kind in Sb:0.005 ~ 0.2% or 2 kinds and/or be selected from Cu:0.03 ~ 1.0%, Ni:0.03 ~ 2.0%, one kind or two or more in B:0.0003 ~ 0.0030% and/or be selected from REM:0.0005 ~ 0.008%, Ca:0.0005 ~ 0.005%, element is selected in one kind or two or more conduct in Mg:0.0005 ~ 0.005%.
What be selected from Nb:0.005 ~ 0.1%, Ti:0.005 ~ 0.1%, V:0.005 ~ 0.1% is one kind or two or more
Nb, Ti, V all separate out with the form of precipitate, are the elements being improved toughness by the miniaturization of tissue.Abrasion Resistant Steels plate of the present invention as required can be one kind or two or more containing what be selected from Nb, Ti, V.
Nb separates out with the form of carboritride, is the element contributing to improving toughness by the miniaturization of tissue.In order to obtain such effect, the content of Nb is set to more than 0.005%.On the other hand, if the content of Nb is more than 0.1%, then weldability declines sometimes.During containing Nb, the content of preferred Nb is limited to the scope of 0.005 ~ 0.1%.Should illustrate, from the viewpoint of organizing miniaturization, more preferably the content of Nb is set to the scope of 0.012 ~ 0.03%.
Ti separates out with the form of TiN, is to help improve the element of toughness by being fixed with of solid solution N.In order to obtain such effect, the content of Ti is set to more than 0.005%.On the other hand, if the content of Ti is more than 0.1%, then sometimes thick carboritride is separated out, and toughness declines.During containing Ti, the content of preferred Ti is limited to the scope of 0.005 ~ 0.1%.Should illustrate, such from the viewpoint of minimizing cost, the content of preferred Ti is limited to the scope of 0.005 ~ 0.03%.
V separates out with the form of carboritride, is the element by will the effect of miniaturization be organized to contribute to improving toughness.In order to obtain such effect, the content of V is set to more than 0.005%.On the other hand, if the content of V is more than 0.1%, then weldability declines sometimes.Therefore, during containing V, the content of preferred V is limited to the scope of 0.005 ~ 0.1%.
Be selected from a kind in Sn:0.005 ~ 0.2%, Sb:0.005 ~ 0.2% or 2 kinds
Sn, Sb are all the elements improving corrosion wear resistance, and Abrasion Resistant Steels plate of the present invention as required can containing a kind that is selected from Sn, Sb or 2 kinds.
Sn with the form stripping of Sn ion by anodic reaction, is played inhibitor effect and suppresses corrosion, thus improving the corrosion wear resistance of steel plate.In addition, Sn forms the oxide film thereon containing Sn at surface of steel plate, suppresses the anodic reaction of steel plate, cathodic reaction, thus improves the corrosion wear resistance of steel plate.In order to obtain these effects, the content of Sn is set to more than 0.005%.On the other hand, if the content of Sn is more than 0.2%, then sometimes cause the deterioration of the ductility of steel plate, toughness.Therefore, during containing Sn, the content of preferred Sn is limited to the scope of 0.005 ~ 0.2%.Should illustrate, such from the viewpoint of minimizing impurity element, more preferably the content of Sn is limited to the scope of 0.005 ~ 0.1%.
Sb, by suppressing the anodic reaction of steel plate and suppressing the hydrogen as cathodic reaction to produce reaction and suppress the corrosion of steel plate, improves the corrosion wear resistance of steel plate.In order to fully such effect, the content of Sb is set to more than 0.005%.On the other hand, if the content of Sb is more than 0.2%, then sometimes cause toughness deterioration.Therefore, during containing Sb, the content of preferred Sb is set to the scope of 0.005 ~ 0.2%.Should illustrate, the content range of preferred Sb is 0.005 ~ 0.1%.
What be selected from Cu:0.03 ~ 1.0%, Ni:0.03 ~ 2.0%, B:0.0003 ~ 0.0030% is one kind or two or more
Cu, Ni, B improve the element of hardenability, and Abrasion Resistant Steels plate of the present invention as required can be one kind or two or more containing what be selected from Cu, Ni, B.
Cu is the element contributing to improving hardenability.In order to obtain such effect, the content of Cu is set to more than 0.03%.On the other hand, if the content of Cu is more than 1.0%, then hot workability declines, and manufacturing cost is also surging.Therefore, during containing Cu, the content of preferred Cu is limited to the scope of 0.03 ~ 1.0%.Should illustrate, such from the viewpoint of reducing cost further, more preferably the content of Cu is limited to the scope of 0.03 ~ 0.5%.
Ni is the element that the low-temperature flexibility improving hardenability and contribute to improving steel plate improves.In order to obtain such effect, the content of Ni is set to more than 0.03%.On the other hand, if the content of Ni is more than 2.0%, then manufacturing cost rises sometimes.During containing Ni, the content of preferred Ni is limited to the scope of 0.03 ~ 2.0%.Should illustrate, such from the viewpoint of reducing manufacturing cost further, more preferably the content of Ni is limited to the scope of 0.03 ~ 0.5%.
B contains with trace the element just contributing to improving hardenability.In order to obtain such effect, the content of B is set to more than 0.0003%.On the other hand, if the content of B is more than 0.0030%, the toughness of steel plate declines sometimes.During containing B, the content of preferred B is limited to the scope of 0.0003 ~ 0.0030%.Should illustrate, normally used CO from the welding suppressing wear-resistant steel plate 2the viewpoint that the low temperature of the low_input_power weld part of welding etc. breaks is considered, more preferably B is limited to the scope of 0.0003 ~ 0.0015%.
What be selected from REM:0.0005 ~ 0.008%, Ca:0.0005 ~ 0.005%, Mg:0.0005 ~ 0.005% is one kind or two or more
REM, Ca, Mg are combined with S to generate sulfide-based inclusion and the element suppressing the generation of MnS.Abrasion Resistant Steels plate of the present invention as required can be one kind or two or more containing what be selected from REM, Ca, Mg.
REM fixes S, the generation of the MnS of the reason suppressing the toughness belonging to steel plate to decline.In order to obtain such effect, the content of REM is set to more than 0.0005%.On the other hand, if the content of REM is more than 0.008%, then the inclusion amount sometimes in steel plate increases, and causes toughness to decline.During containing REM, the content of preferred REM is limited to the scope of 0.0005 ~ 0.008%.Should illustrate, the content range of preferred REM is 0.0005 ~ 0.0020%.
Ca fixes S, suppresses the generation of the MnS belonging to the reason that toughness declines.In order to obtain such effect, the content of Ca is set to more than 0.0005%.On the other hand, if the content of Ca is more than 0.005%, then the inclusion amount sometimes in steel plate increases, and causes toughness to decline on the contrary.During containing Ca, the content of preferred Ca is limited to the scope of 0.0005 ~ 0.005%.Should illustrate, the scope of the content of preferred Ca is 0.0005 ~ 0.0030%.
Mg fixes S, the generation of the MnS of the reason suppressing the toughness belonging to steel plate to decline.In order to obtain such effect, the content of Mg is set to more than 0.0005%.On the other hand, if the content of Mg is more than 0.005%, then the inclusion amount sometimes in steel plate increases, and causes toughness to decline on the contrary.During containing Mg, the content of preferred Mg is limited to the scope of 0.0005 ~ 0.005%.Should illustrate, the content range of preferred Mg is 0.0005 ~ 0.0040%.
The scope more than wear-resistant steel plate of the present invention stated and with meet DI* be more than 45 mode contain above-mentioned composition.DI* is defined by following formula (1).Should illustrate, when calculating DI*, the element do not contained in the element that formula (1) is recorded can be regarded as zero.
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)×(1.75×V+1) (1)
(wherein, C, Si, Mn, Cu, Ni, Cr, Mo, V: the content (quality %) of each element)
DI* lower than 45 time, apart from the depth of hardening of surface of steel plate lower than 10mm, as the lifetime of wear-resistant steel plate.Therefore, DI* is limited to more than 45.Should illustrate, the scope of preferred DI* is more than 75.
Remainder beyond mentioned component is Fe and inevitable impurity.
Then, the tissue of wear-resistant steel plate of the present invention and character are described.
Wear-resistant steel plate of the present invention has above-mentioned composition, and has with quenching state martensitic phase for principal phase and original austenite (γ) particle diameter is the tissue of less than 30 μm.In addition, the surface hardness of wear-resistant steel plate of the present invention with Brinell tester HBW10/3000 for more than 450.Should illustrate, " principal phase " mentioned here refers to the phase counting more than 90% with area occupation ratio.
Quenching state martensitic phase: count more than 90% with area occupation ratio
The phase per-cent of quenching state martensitic phase in area occupation ratio lower than 90% time, cannot guarantee that steel plate has desired hardness.Therefore, above-mentioned area occupation ratio lower than 90% time, the wearability of steel plate declines cannot guarantee desired wearability, and also cannot guarantee sufficient low-temperature flexibility.In addition, for tempered martensite phase, because Cr during tempering generation cementite forms carbide together with Mo and Fe.Due to the formation of this carbide, to guaranteeing that effective solid solution Cr and Mo of erosion resistance reduces.Therefore, martensitic phase is made to be the quenching state martensitic phase not carrying out tempering.Should illustrate, the phase per-cent of quenching state martensitic phase is preferably more than 95% in area occupation ratio, is more preferably more than 98%.
Former γ particle diameter: less than 30 μm
Even if can guarantee that the phase per-cent of quenching state martensitic phase counts more than 90% with area occupation ratio, if former γ particle diameter becomes thick more than 30 μm, then the low-temperature flexibility of steel plate still declines.Should illustrate, former γ particle diameter adopts the tissue corroded with opticmicroscope (multiplying power: 400 times) observations picric acid corrosive fluid, the value of trying to achieve based on the regulation of JIS G0551.
In addition, there is above-mentioned composition, the surface hardness of of the present invention wear-resistant steel plate of tissue counts more than 450 with Brinell hardness HBW10/3000.
Surface hardness: count more than 450 with Brinell hardness HBW10/3000
Surface hardness in Brinell hardness HBW10/3000 lower than 450 time, as the lifetime of wear-resistant steel plate.Therefore, surface hardness is set to more than 450 in Brinell hardness HBW10/3000.Should illustrate, Brinell hardness is the value measured based on the regulation of JIS Z 2243.
Next, the preferred manufacture method of wear-resistant steel plate of the present invention is described.
After the steel material of above-mentioned composition is cast, keep not cooling when the temperature of regulation directly reheating, or reheat after cooling, carry out hot rolling, the steel plate of the size shape desired by formation.
Should illustrate, the manufacture method of steel material does not need to be particularly limited to.Preferably with the molten steel (molten steel) of the above-mentioned compositions of known melting method melting such as converter, make the steel materials such as the slab (slab) of specified dimension by known castmethods such as Continuous casting processes (continuous casting).Should illustrate, naturally also can make steel material by ingot casting (ingot casting)-cogging method (blooming method).
Reheat temperature: 950 ~ 1250 DEG C
When reheating temperature lower than 950 DEG C, it is excessive that ambassador's rolling load is crossed in resistance to deformation (deformation resistance), sometimes cannot carry out hot rolling.On the other hand, reheating under the high temperature of temperature more than 1250 DEG C, the coarsening of crystal grain becomes obvious, sometimes cannot guarantee desired high tenacity.Therefore, limit temperature is preferably reheated the scope of 950 ~ 1250 DEG C.
Next to the steel material through reheating or the steel material enforcement hot rolling not keeping the temperature specified through reheating, the steel plate of desired size shape is made.Hot-rolled condition does not need to be particularly limited to.The direct quenching process of quenching is carried out immediately after preferred enforcement hot rolling terminates.Should illustrate, quenching starts temperature and is preferably Ar 3temperature more than transformation temperature.Starting temperature to make quenching is Ar 3temperature more than transformation temperature, preferred hot rolling end temp is Ar 3temperature more than transformation temperature, namely more than 800 DEG C.In addition, if hot rolling end temp is too high, coarse grains sometimes, therefore hot rolling end temp is preferably less than 950 DEG C.As long as the speed of cooling of quenching is just not particularly limited more than the speed of cooling forming martensitic phase.In order to prevent martensitic phase self-tempering (auto-temper), martensitic volume fraction is reduced, when being generated cementite by tempering, Cr forms carbide together with Mo and Fe, thus make guaranteeing the phenomenon that effective solid solution Cr and Mo of erosion resistance reduces, speed of cooling is more high better within the bounds of possibility.Cool with 65 ~ 75 DEG C/s when preferred thickness of slab is 5 ~ 15mm, cool with 40 ~ 55 DEG C/s when thickness of slab is 16 ~ 22mm, cool with 30 ~ 40 DEG C/s when thickness of slab is 22 ~ 28mm, cool with 20 ~ 30 DEG C/s when thickness of slab is 29 ~ 35mm.Further, cooling stops temperature being preferably less than 300 DEG C, is more preferably less than 200 DEG C.Should illustrate, in this specification sheets, speed of cooling refers to that carrying out heat trnasfer-thermal conduction to the temperature of the part of steel plate central authorities calculates and the speed of cooling obtained.
In addition, also can be embodied in after carrying out letting cool (air cooling) after hot rolling terminates, reheat the Heating temperature to regulation, carry out the process of quenching further to carry out the direct quenching process of quenching after replacing hot rolling to terminate immediately.Should illustrating, as reheating temperature, being preferably 850 ~ 950 DEG C.Just be not particularly limited as long as the speed of cooling of the quenching after reheating is more than the speed of cooling of formation martensitic phase.In order to prevent martensitic phase self-tempering (auto-temper), martensitic volume fraction is reduced, when being generated cementite by tempering, Cr forms carbide together with Mo and Fe, thus make guaranteeing the phenomenon that effective solid solution Cr and Mo of erosion resistance reduces, speed of cooling is more high better within the bounds of possibility, cool with 65 ~ 75 DEG C/s when preferred thickness of slab is 5 ~ 15mm, cool with 40 ~ 55 DEG C/s when thickness of slab is 16 ~ 22mm, cool with 30 ~ 40 DEG C/s when thickness of slab is 22 ~ 28mm, cool with 20 ~ 30 DEG C/s when thickness of slab is 29 ~ 35mm.Further, in order to prevent martensitic phase self-tempering (auto-temper), preferably cooling stops temperature to be less than 300 DEG C, is more preferably less than 200 DEG C.
Should illustrating, in order to form quenching state martensitic stucture, after the treatment, not implementing temper.
Below, based on embodiment, the present invention is described further.
Embodiment
With the molten steel of the composition shown in vacuum melting stove melting table 1, cast in the mould, make 150kgf steel ingot (steel material).These steel materials are reheated to the Heating temperature shown in table 2 (table 2-1, table 2-2, table 2-3), carry out hot rolling under the conditions shown in Table 2.Then, under the conditions shown in Table 2 a part of steel plate is carried out quenching immediately after hot rolling terminates the direct quenching process (DQ) of (direct quenching).In addition, carry out quench in furnace process (RQ) under the conditions shown in Table 2 to another part steel plate, that is, hot rolling terminates rear air cooling, reheats further to the temperature shown in table 2, quenches.Should illustrate, in the example shown in table 2-3, also show in DQ or RQ from the speed of cooling of 800 DEG C to 500 DEG C.Generally speaking, the phase transformation of common C-Mn steel in cooling, almost 800 DEG C of beginnings, terminates near 500 DEG C.Therefore, have a significant impact from the phase transformation movement of speed of cooling to steel of 800 DEG C to 500 DEG C.Therefore, the representative speed of cooling of the phase transformation movement for inferring steel is widely used as from the speed of cooling of 800 DEG C to 500 DEG C.
From the steel plate acquisition test sheet obtained, implement structure observation, superficial hardness test, Charpy impact test, anti-corrosion wear test.Test method is as follows.In addition, the result of structure observation, superficial hardness test, Charpy impact test, anti-corrosion wear test is shown in table 3 (table 3-1, table 3-2, table 3-3).
(1) structure observation
First, the mode becoming the cross section in the direction parallel with rolling direction from thickness of slab 1/2 position of the steel plate obtained with sightingpiston gathers structure observation test film.Then, the sightingpiston of structure observation test film is ground, corroded with picric acid corrosive fluid and former γ grain is occurred.Then, with opticmicroscope (multiplying power: 400 times), sightingpiston is observed, measure the projection circle equivalent footpath of each 100 Geju City γ grains, calculate the mean value of the value obtained.Using the old γ particle diameter of this mean value as this steel plate.
In addition, film like test specimen (transmission electron microscope structure observation test film) is similarly gathered from thickness of slab 1/4 position of the steel plate obtained.Then, film like test specimen is made film through grinding, grinding (mechanical mill, electrolytic polishing).Then, transmission electron microscope (multiplying power: 20000 times) is utilized to observe each 20 visual fields, place to above-mentioned film, the region of separating out not having cementite, as martensitic phase region, measures its area, and the ratio (%) be used in shared by organized whole represents.Using this ratio as martensite percentage (area occupation ratio).Should illustrate, the judgement of its kind has also been carried out to the phase that cementite is separated out.
(2) superficial hardness test
From the steel plate collection surface measurement of hardness test film obtained, based on the regulation of JIS Z 2243 (1998), chart surface hardness HBW10/3000.Measurement of hardness uses the tungsten hard sphere of 10mm, and load is set to 3000kgf.
(3) Charpy impact test
Gather V notched specimen in thickness of slab 1/4 position of the steel plate obtained from the direction (C direction) vertical with rolling direction, based on the regulation of JIS Z 2242 (1998), implement Charpy impact test.Obtaining test temperature is absorption energy vE under the condition of ﹣ 40 DEG C ﹣ 40(J).Should illustrate, test film number is set to each 3, using the absorption energy vE of its arithmetical av as this steel plate ﹣ 40.By vE ﹣ 40steel plate for more than 30J is evaluated as the steel plate of tenacity excellent.
(4) anti-corrosion wear test
From the station acquisition wearing test sheet apart from surperficial 1mm of the steel plate obtained (size: 10mm is thick × 25mm is wide × 75mm is long).These test films are arranged on wear testing machine, implement wearing test.
By wearing test sheet after the mode that the face of 25mm × 75mm becomes the tangent to periphery direction of rotational circle installs, with water jacket cover butter sheet and rotor, internally to import wearing and tearing material with the rotational axis vertical of trier rotor.As wearing and tearing material, the silica sand that to use median size be 0.65mm and concentration adjustment are the material that the NaCl aqueous solution of 15000 quality ppm is obtained by mixing in the mode that the weight ratio of silica sand and the NaCl aqueous solution becomes 3:2.
Test conditions is with rotor: 600 beats/min, water jacket: the condition of 45 beats/min of each spinnings.Rotate after reaching total 10800 times to the rotation times of rotor, terminate test.After off-test, measure the weight of each test film.Then, calculate the difference (=weight reduction) of the rear weight of test and initial weight, by tensile strength 400MPa level Rolled Steel For General Structure SS400 (Rolled steels for general structure, Tensile strength 400MPa class) the weight reduction of (JIS G3101) (conventional example) as benchmark value, calculate wear-resistant than (=(benchmark value)/(the weight reduction of test film)).Be the average evaluation of more than 1.5 by wear-resistant ratio be " corrosion wear resistance excellent ".
[table 2-1]
* DQ: direct quenching, RQ: quench in furnace
[table 2-2]
* DQ: direct quenching, RQ: quench in furnace
[table 3-1]
[table 3-2]
[table 3-3]
The present invention's example all has surface hardness and counts more than 450 such high surface hardness with HBW10/3000, vE ﹣ 40: the low-temperature flexibility of the excellence of more than 30J and wear-resistant ratio: the corrosion wear resistance of the excellence of more than 1.5.Further, high with the martensite percentage of the steel plate of high speed of cooling cooling.Particularly martensite percentage be more than 98% steel plate and cold martensite percentage lower than 98% the steel plate that forms of identical component compared with, there is corrosion wear resistance excellent especially.On the other hand, in the comparative example departed from the scope of the present invention, or surface hardness is low or low-temperature flexibility declines or corrosion wear resistance declines or wherein more than 2 decline.

Claims (6)

1. a wear-resistant steel plate for low-temperature flexibility and corrosion wear resistance excellence, is characterized in that, has following one-tenth and is grouped into:
C:0.23 ~ 0.35%, Si:0.05 ~ 1.00%, Mn:0.1 ~ 2.0%, below P:0.020%, below S:0.005%, Al:0.005 ~ 0.100%, Cr:0.03 ~ 2.0%, Mo:0.03 ~ 1.0% is contained in mass % in the mode that the satisfied DI* defined by following formula (1) is more than 45, remainder is made up of Fe and inevitable impurity
Further, have with quenching state martensitic phase for principal phase and original austenite particle diameter is the tissue of less than 30 μm,
Surface hardness counts more than 450 with Brinell hardness HBW10/3000,
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)×(1.75×V+1)······(1)
In formula (1), C, Si, Mn, Cu, Ni, Cr, Mo and V are the content of each element, and unit is quality %.
2. wear-resistant steel plate according to claim 1, is characterized in that, on the basis of described composition, one kind or two or more containing what be selected from Nb:0.005 ~ 0.1%, Ti:0.005 ~ 0.1% and V:0.005 ~ 0.1% in mass % further.
3. wear-resistant steel plate according to claim 1 and 2, is characterized in that, on the basis of described composition, further in mass % containing a kind that is selected from Sn:0.005 ~ 0.2% and Sb:0.005 ~ 0.2% or 2 kinds.
4. according to the wear-resistant steel plate in claims 1 to 3 described in wantonly 1, it is characterized in that, on the basis of described composition, one kind or two or more containing what be selected from Cu:0.03 ~ 1.0%, Ni:0.03 ~ 2.0% and B:0.0003 ~ 0.0030% in mass % further.
5. according to the wear-resistant steel plate in Claims 1 to 4 described in wantonly 1, it is characterized in that, on the basis of described composition, one kind or two or more containing what be selected from REM:0.0005 ~ 0.008%, Ca:0.0005 ~ 0.005% and Mg:0.0005 ~ 0.005% in mass % further.
6. according to the wear-resistant steel plate in Claims 1 to 5 described in wantonly 1, it is characterized in that, the content of described quenching state martensitic phase counts more than 98% with volume fraction.
CN201380048598.5A 2012-09-19 2013-09-13 Wear-resistant steel plate having excellent low-temperature toughness and corrosion wear resistance Pending CN104685088A (en)

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BR112015005951B1 (en) 2019-09-17
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WO2014045552A1 (en) 2014-03-27
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AU2013319621A1 (en) 2015-02-26
US20150232971A1 (en) 2015-08-20

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