Patent Application
20130216422
The present invention relates to an abrasion resistant steel plate or steel sheet having a plate thickness of 4 mm or more preferably used in construction machines, industrial machines, shipbuilding, steel pipes, civil engineering, architecture or the like, and more particularly to an abrasion resistant steel plate or steel sheet which exhibits excellent weld toughness and excellent delayed fracture resistance.
When a hot-rolled steel plate is employed for making steel structural products, machines, devices or the like in construction machines, industrial machines, shipbuilding, steel pipes, civil engineering, architecture or the like, there may be a case where the steel plates are required to possess abrasion resistant property. Conventionally, to impart excellent abrasion resistant property to a steel material, hardness is increased in general, and hardness of the steel material can be remarkably enhanced by obtaining the steel material into the martensite single phase microstructure. The increase of an amount of solid solution carbon is also effective for enhancing hardness of martensite microstructure per se.
Accordingly, the abrasion resistant steel plate exhibits high cold cracking susceptibility so that the steel plate exhibits inferior weld toughness in general whereby when the abrasion resistant steel plate is used in obtaining the welded steel structure, in general, the abrasion resistant steel plate is laminated to a surface of a steel member which is brought into contact with rock, soil and sand or the like as a liner. For example, with respect to a vessel of a damped motor lorry, there has been known a case where the vessel is assembled by welding using mild steel and, thereafter, an abrasion resistant steel plate is laminated to only a front surface of the vessel which is brought into contact with earth and sand.
However, in the manufacturing method in which the abrasion resistant steel plate is laminated to the welded steel structure after the welded steel structure has been assembled, the labor for the manufacture and a manufacturing cost are increased. Accordingly, there has been a demand for an abrasion resistant steel plate which can be used as a strength member of the welded steel structure.
Patent document 1 relates to an abrasion resistant steel plate which exhibits excellent delayed fracture resistance and a method of manufacturing the abrasion resistant steel plate. In patent document 1, there is the description that, to improve the delayed fracture resistance, steel which further contains one, two or more kinds of components selected from a group consisting of Cu, V, Ti, B and Ca in the composition of a type containing low-Si, low-P, low-S, Cr, Mo and Nb is subjected to direct quenching (hereinafter also referred to as DQ), and tempering is performed when necessary.
Patent document 2 relates to steel having high abrasion resistant property and a method of manufacturing a steel product. In patent document 2, there is described steel which has the composition composed of a 0.24 to 0.3C—Ni, Cr, Mo, B system, satisfies a parameter formula constituted of contents of these elements, and includes martensite containing 5 to 15 volume % of austenite or martensitic structure and bainitic structure thus enhancing abrasion resistant property. Patent document 2 also describes that the steel having the above-mentioned components is cooled at a cooling rate of 1° C./sec or more at a temperature between an austenitizing temperature and 450° C.
Patent document 3 relates to an abrasion resistant steel material which exhibits excellent toughness and excellent delayed fracture resistance and a method of manufacturing the abrasion resistant steel material. In patent document 3, there is described a steel material which has the composition containing Cr, Ti, and B as indispensable components, wherein a surface layer is formed of tempered martensite, an internal part is formed of tempered martensite and tempered lower bainitic structure, and an aspect ratio of prior austenite grain diameter between the wall thickness direction and the rolling direction is defined. Patent document 3 also describes that the steel having the content composition is subject to hot rolling at a temperature of 900° C. or below and at a cumulative reduction ratio of 50% or more and, thereafter, is directly quenched and tempered.
Patent document 4 relates to an abrasion resistant steel material which exhibits excellent toughness and excellent delayed fracture resistance and a method of manufacturing the abrasion resistant steel material. In patent document 4, there is described a steel material which has the composition containing Cr, Ti and B as indispensable components, wherein a surface layer is formed of martensite, and an internal part is formed of the mixed structure of martensite and lower bainitic structure or lower bainitic single-phase structure, and an elongation rate of prior austenite grains expressed by an aspect ratio between prior austenite grain diameter at a plate thickness center portion and prior austenite grain diameter in the rolling direction is defined. Patent document 4 also describes that the steel having the composition is subjected to hot rolling at a temperature of 900° C. or below and at a cumulative reduction ratio of 50% or more and, thereafter, is directly quenched.
Patent document 5 relates to abrasion resistant steel which exhibits excellent weldability, excellent abrasion resistant property and excellent corrosion resistance, and a method of manufacturing the abrasion resistant steel. In patent document 5, there is described steel which contains 4 to 9 mass % of Cr as an indispensable element, contains one kind or two kinds of Cu and Ni and satisfies a parameter formula constituted of contents of specific components. Patent document 5 also describes that the steel having the composition is subjected to hot rolling at a temperature of 950° C. or below and at a cumulative reduction ratio of 30% or more and, thereafter, the steel is reheated at a temperature of Ac3 or more and is quenched.
The most serious problem relating to the lowering of toughness when a steel material is welded is the deterioration of toughness at a bond area of a fusion line. In abrasion resistant steel having martensite structure in a quenched state, the deterioration of toughness which is referred to as low-temperature tempering embrittlement arises as a problem also in a welded heat affected zone (hereinafter also referred to as HAZ) reheated to a temperature around 300° C. which is away from the fusion line. It is thought that low-temperature tempering embrittlement is brought about by a synergistic action between a morphology change of carbide in martensite and the intergranular segregation of impurity elements or the like.
In a region which is reheated at a low-temperature tempering embrittlement temperature, hydrogen which invades a weld from a shielding gas at the time of welding and a residual stress generated by welding heat overlap with each other so that delayed fracture (cracks which occur in the weld are referred to as low-temperature cracks in general) is liable to occur and, particularly, delayed fracture is liable to occur in an abrasion resistant steel having high strength.
Accordingly, in applying an abrasion resistant steel plate to a strength member of a welded structure, it is necessary to enhance toughness of the bond area and the welded heat affected zone reheated to a temperature around 300° C. which is away from a fusion line. However, in the conventional abrasion resistant steel plate, cold cracking susceptibility of the weld is high and hence, to prevent cold cracks, it is necessary to discharge hydrogen in the steel plate and to lower a residual stress in the steel plate by performing treatments such as preheating and post heating before and after welding.
Patent documents 1 and 2 fail to describe the enhancement of weld toughness in the abrasion resistant steel, and patent documents 3 and 4 also define the microstructure aiming at the enhancement of toughness of a base material. Although patent document 5 studies weldability and abrasion resistant property of a weld, the study does not aim at the enhancement of weld toughness. That is, the abrasion resistant steels proposed in patent documents 1 to 5 and the like are less than optimal with respect to the improvement of both weld toughness and delayed fracture resistance.
Accordingly, it is an object of the present invention to provide an abrasion resistant steel plate which exhibits excellent weld toughness and excellent delayed fracture resistance without inducing lowering of productivity and the increase in a manufacturing cost. In the present invention, weld toughness means toughness of a welded heat affected zone, and the excellent weld toughness means particularly that the toughness is excellent in a bond area and a low-temperature tempering embrittlement temperature area.
To achieve the above-mentioned object, inventors of the present invention have made extensive studies on various factors which determine chemical components of a steel plate, a method of manufacturing the steel plate and the microstructure of the steel plate so as to secure weld toughness and delayed fracture resistance with respect to an abrasion resistant steel plate, and have made following findings.
1. To secure excellent abrasion resistant property, it is indispensable to form the base microstructure or the main microstructure of the steel plate into martensite. For this end, it is important to strictly control the chemical composition of the steel plate thus securing quenching property.
2. To achieve the excellent weld toughness, it is necessary to suppress grain particles in the bond area from becoming coarse, and for this end, it is effective to make use of a pinning effect by dispersing fine precipitates in the steel plate.
3. To secure the excellent toughness and to suppress delayed fracture in a low-temperature tempering embrittlement temperature area of the welded heat affected zone, it is important to properly control quantities of alloy elements such as C, Mn, Cr, P.
The present invention has been made by further studying the above-mentioned findings. That is, the present invention is directed to:
1. An abrasion resistant steel plate having excellent weld toughness and excellent delayed fracture resistance, and having a composition containing by mass % 0.20 to 0.30% C, 0.05 to 1.0% Si, 0.40 to 1.2% Mn, 0.010% or less P, 0.005% or less S, 0.40 to 1.5% Cr, 0.005 to 0.025% Nb, 0.005 to 0.03% Ti, 0.1% or less Al, 0.01% or less N, and Fe and unavoidable impurities as a balance, wherein hardenability index DI* expressed by a formula (1) is 45 or more, and a base phase of the microstructure is formed of martensite.
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)×(1.5×W+1) (1),
wherein the respective element symbols are contents (mass %) of the elements.
2. The abrasion resistant steel plate having excellent weld toughness and excellent delayed fracture resistance described in 1, wherein the steel composition further contains by mass % one, two or more kinds of components selected from a group consisting of 0.05 to 1.0% Mo, 0.05 to 1.0% W, and 0.0003% to 0.0030% B.
3. The abrasion resistant steel plate having excellent weld toughness and excellent delayed fracture resistance described in 1 or 2, wherein the steel composition further contains by mass % one, two or more kinds of components selected from a group consisting of 1.5% or less Cu, 2.0% or less Ni, and 0.1% or less V.
4. The abrasion resistant steel plate having excellent weld toughness and excellent delayed fracture resistance described in any one of 1 to 3, wherein the steel composition further contains by mass % one, two or more kinds of components selected from a group consisting of 0.008% or less REM, 0.005% or less Ca, and 0.005% or less Mg.
5. The abrasion resistant steel plate having excellent weld toughness and excellent delayed fracture resistance described in any one of 1 to 4, wherein surface hardness of the steel plate is 400 HBW10/3000 or more in Brinell hardness.
6. The abrasion resistant steel plate having excellent weld toughness and excellent delayed fracture resistance described in any one of 1 to 5, wherein hardenability index DI* is 180 or less.
7. The abrasion resistant steel plate having excellent weld toughness and excellent delayed fracture resistance described in any one of 1 to 6, wherein the steel plate satisfies a following formula (2).
C+Mn/4−Cr/3+10P≦0.47 (2),
wherein the respective element symbols are contents (mass %) of the elements.
According to the present invention, it is possible to acquire the abrasion resistant steel plate having excellent weld toughness and excellent delayed fracture resistance. The present invention largely contributes to the enhancement of manufacturing efficiency and safety at the time of manufacturing a steel structure thus acquiring an industrially remarkable effect.
The present invention defines the composition and the microstructure.
In the explanation made hereinafter, % indicates mass %. C: 0.20 to 0.30%
C is an important element for increasing hardness of martensite and for allowing the steel plate to secure the excellent abrasion resistant property. It is necessary for the steel plate to contain 0.20% or more C to acquire such effects. On the other hand, when the content of C exceeds 0.30%, not only weldability is deteriorated but also toughness of a bond area and toughness of a low-temperature tempering region are deteriorated. Accordingly, content of C is limited to a value which falls within a range from 0.20 to 0.30%. The content of C is preferably limited to a value which falls within a range from 0.20 to 0.28%.
Si acts as a deoxidizing agent, and not only Si is necessary for steel making but also Si has an effect of increasing hardness of a steel plate by solid solution strengthening where Si is present in steel in a solid solution state. Further, Si has an effect of suppressing the deterioration of toughness in a tempering embrittlement area of a welded heat affected zone. It is necessary for the steel plate to contain 0.05% or more Si to acquire such an effect. On the other hand, when the content of Si exceeds 1.0%, toughness of the welded heat affected zone is remarkably deteriorated. Accordingly, the content of Si is limited to a value which falls within a range from 0.05 to 1.0%. The content of Si is preferably limited to a value which falls within a range from 0.07 to 0.5%.
Mn has an effect of increasing hardenability of steel, and it is necessary for the steel plate to contain 0.40% or more Mn to secure hardness of a base material. On the other hand, when the content of Mn exceeds 1.2%, not only toughness, ductility and weldability of the base material are deteriorated, but also intergranular segregation of P is accelerated thus accelerating the generation of delayed fracture. Accordingly, the content of Mn is limited to a value which falls within a range from 0.40 to 1.2%. The content of Mn is preferably limited to a value which falls within a range from 0.40 to 1.1%.
When the content of P exceeds 0.010%, P is segregated in a grain boundary, the segregated P becomes an initiation point of delayed fracture, and deteriorates toughness of a welded heat affected zone. Accordingly, an upper limit of the content of P is set to 0.010% and it is desirable that the content of P is set as small as possible. Since the excessive reduction of P pushes up a refining cost and becomes economically disadvantageous, the content of P is desirably set to 0.002% or more.
S deteriorates low-temperature toughness and ductility of a base material and hence, the content of S is desirably set small with an allowable upper limit of 0.005%.
Cr is an important alloy element in the present invention, and has an effect of increasing hardenability of steel and also has an effect of suppressing the deterioration of toughness in the tempering embrittlement area of the welded heat affected zone. This is because the inclusion of Cr delays the diffusion of C in the steel plate and hence, when the steel plate is reheated to a temperature region where the low-temperature tempering embrittlement occurs, morphology change of carbide in martensite can be suppressed. It is necessary for the steel plate to contain 0.40% or more of Cr to acquire such an effect. On the other hand, when the content of Cr exceeds 1.5%, the effect is saturated so that not only does it become economically disadvantageous but also weldability is lowered. Accordingly, the content of Cr is limited to a value which falls within a range from 0.40 to 1.5%. The content of Cr is preferably limited to a value which falls within a range from 0.40 to 1.2%.
Nb is an important element having both an effect of improving toughness of the welded heat affected zone and an effect of suppressing the occurrence of delayed fracture by making the microstructure of the base material and the welded heat affected zone finer by causing the precipitation of carbonitride and also by fixing solid solution N. It is necessary for the steel plate to contain 0.0050% or more Nb to acquire such effects. On the other hand, when the content of Nb exceeds 0.025%, coarse carbonitride precipitates and there may be a case where the coarse carbonitride becomes an initiation point of fracture. Accordingly, the content of Nb is limited to a value which falls within a range from 0.005 to 0.025%. The content of Nb is preferably limited to a value which falls within a range from 0.007 to 0.023%.
Ti has an effect of suppressing grains in the bond area from becoming coarse by forming TiN due to fixing of solid solution N, and also has an effect of suppressing the deterioration of toughness and the occurrence of delayed fracture in the low-temperature tempering temperature region due to the decrease of solid solution N. It is necessary for the steel plate to contain 0.005% or more Ti to acquire such effects. On the other hand, when the content of Ti exceeds 0.03%, TiC precipitates so that toughness of the base material is deteriorated. Accordingly, the content of Ti is limited to a value which falls within a range from 0.005 to 0.03%. The content of Ti is preferably limited to a value which falls within a range from 0.007 to 0.025%.
Al: 0.1% or less
Al acts as a deoxidizing agent and is most popularly used in a molten steel deoxidizing process of a steel plate. Further, by forming AlN by fixing solid solution N in steel, Al has an effect of suppressing grains in a bond area from becoming coarse and an effect of suppressing the deterioration of toughness and the occurrence of delayed fracture in a low-temperature tempering temperature region due to the reduction of solid solution N. On the other hand, when the content of Al exceeds 0.1%, Al is mixed into weld metal at the time of welding thus deteriorating toughness of weld metal. Accordingly, the content of Al is limited to 0.1% or less. The content of Al is preferably limited to a value which falls within a range from 0.01 to 0.07%.
N forms a nitride with Nb or Ti, and has an effect of suppressing grains of welded heat affected zone from becoming coarse. However, when the content of N exceeds 0.01%, toughness of a base material and weld toughness is remarkably lowered and hence, the content of N is limited to 0.01% or less. The content of N is preferably limited to a value which falls within a range from 0.0010 to 0.0070%. A balance is Fe and unavoidable impurities.
According to the present invention, to further enhance properties of the steel plate, in addition to the above-mentioned basic component system, the steel plate may contain one, two or more kinds of components selected from a group consisting of Mo, W, B, Cu, Ni, V, REM, Ca and Mg.
Mo is an element effective for remarkably increasing hardenability thus increasing hardness of a base material. The content of Mo may preferably be 0.05% or more for acquiring such an effect. However, when the content of Mo exceeds 1.0%, Mo adversely influences toughness, ductility and weld crack resistance of the base material. Accordingly, the content of Mo is set to 1.0% or less.
W is an element effective for remarkably increasing hardenability thus increasing hardness of a base material. The content of W may preferably be 0.05% or more for acquiring such an effect. However, when the content of W exceeds 1.0%, W adversely influences toughness, ductility and weld crack resistance of the base material. Accordingly, the content of W is set to 1.0% or less.
B is an element effective for remarkably increasing hardenability with addition of a trace amount of B thus increasing hardness of a base material. The content of B may preferably be 0.0003% or more for acquiring such an effect. However, when the content of B exceeds 0.0030%, B adversely influences toughness, ductility and weld crack resistance of the base material. Accordingly, the content of B is set to 0.0030% or less.
All of Cu, Ni and V are elements which contribute to the enhancement of strength of steel, and the steel plate may contain proper amounts of Cu, Ni, V depending on strength which the steel plate requires.
Cu is an element effective for increasing hardenability thus increasing hardness of the base material. The content of Cu may preferably be 0.1% or more for acquiring such an effect. However, when the content of Cu exceeds 1.5%, the effect is saturated and Cu causes hot brittleness thus deteriorating surface property of a steel plate. Accordingly, the content of Cu is set to 1.5% or less.
Ni is an element effective for increasing hardenability thus increasing hardness of the base material. The content of Ni may preferably be 0.1% or more for acquiring such an effect. However, when the content of Ni exceeds 2.0%, the effect is saturated so that it becomes economically disadvantageous. Accordingly, the content of Ni is set to 2.0% or less.
V is an element effective for increasing hardenability thus increasing hardness of the base material. The content of V may preferably be 0.01% or more for acquiring such an effect. However, when the content of V exceeds 0.1%, toughness and ductility of the base material is deteriorated. Accordingly, the content of V is set to 0.1% or less.
All of REM, Ca and Mg contribute to the enhancement of toughness, and these elements are selectively added corresponding to properties which the steel plate desires. When REM is added, the content of REM may preferably be 0.002% or more. On the other hand, when the content of REM exceeds 0.008%, the effect is saturated. Accordingly, an upper limit of REM is set to 0.008%.
When Ca is added, the content of Ca may preferably be 0.0005% or more. On the other hand, when the content of Ca exceeds 0.005%, the effect is saturated. Accordingly, an upper limit of Ca is set to 0.005%.
When Mg is added, the content of Mg may preferably be 0.001% or more. On the other hand, when the content of Mg exceeds 0.005%, the effect is saturated. Accordingly, an upper limit of Mg is set to 0.005%.
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)×(1.5×W+1) (1),
wherein the respective element symbols are contents (mass %) of the elements.
This parameter: DI* (hardenability index) is defined to form the base structure of the base material into martensite thus imparting excellent abrasion resistant property to the base structure within the range of the above-mentioned composition, and a value of the parameter is set to 45 or more. When the value of the parameter is set to less than 45, a quenching depth from a surface layer in the plate thickness direction becomes less than 10 mm and hence, a lifetime of the steel plate as the abrasion resistant steel plate is shortened.
When the value DI* of the parameter exceeds 180, the base structure of the base material is martensite and hence, the base structure exhibits favorable abrasion resistant property. However, low-temperature crack property at the time of welding and low-temperature weld toughness are deteriorated. Accordingly, the value of the parameter DI* is preferably set to 180 or less. The value of the parameter DI* is more preferably set to a value which falls within a range from 50 to 160.
C+Mn/4−Cr/3+10P≦0.47 (2),
wherein the respective element symbols are contents (mass %) of the elements.
When the basic structure of the base material of the steel plate is formed of martensite and has the composition which exhibits excellent toughness in both the bond area and the low-temperature tempering embrittlement area when welding is performed, a value of the parameter: C+Mn/4−Cr/3+10P is set to 0.47 or less within a range of the above-mentioned composition. Although the base structure of the base material is held in martensite and exhibits favorable abrasion resistant property even when the value of the parameter exceeds 0.47, weld toughness is remarkably deteriorated. The value of parameter may preferably be 0.45 or less.
According to the present invention, to enhance abrasion resistant property, a base phase or a main phase of the microstructure of a steel plate is defined to martensite. The structure such as bainite or ferrite other than martensite lowers abrasion resistant property and hence, it is preferable not to mix such structure into martensite as much as possible. However, when a total area ratio of these structures is less than 10%, the influence exerted by these structures can be ignored. Further, when surface hardness of the steel plate is less than 400 HBW10/3000 in Brinell hardness, a lifetime of the steel plate as abrasion resistant steel is shortened. Accordingly, it is desirable to set the surface hardness to 400 HBW10/3000 or more in Brinell hardness.
The microstructure of the bond area is the mixed structure of martensite and bainite. The structure such as ferrite other than martensite and bainite lowers abrasion resistant property and hence, it is preferable not to mix such structure as much as possible. However, when a total area ratio of these structures is less than 20%, the influence exerted by these structures can be ignored.
Further, to secure toughness of the bond area, it is preferable that carbonitride particles of Nb and Ti having an average particle size of 1 μm or less are present at a rate of 1000 pieces/mm2 or more, an average particle size of prior austenite is less than 200 μm, and an average particle size of lower microstructure surrounded by a large tilt grain boundary having a radial hook of 15° or more is less than 70 μm.
The abrasion resistant steel according to the present invention can be manufactured under the following manufacturing conditions. In the explanation made hereinafter, the indication “° C.” relating to temperature means temperature at ½ position of a plate thickness. It is preferable that a molten steel having the above-mentioned composition is produced by a known molten steel producing method, and the molten steel is formed into a raw steel material such as a slab having a predetermined size by a continuous casting process or an ingot-making/blooming method.
Next, the obtained raw steel material is immediately subjected to hot rolling without cooling or is subjected to hot rolling following heating at a temperature of 950 to 1250° C. after cooling thus obtaining a steel plate having a desired plate thickness. Immediately after hot rolling, water cooling is performed or quenching is performed after reheating. Thereafter, when necessary, tempering is performed at a temperature of 300° C. or below.
Steel slabs which were prepared with various compositions shown in Table 1 by way of a steel converter, ladle refining and a continuous casting method were heated at a temperature of 1000 to 1250° C. and, thereafter, the steel slabs were subjected to hot rolling under manufacturing conditions shown in Table 2. Water cooling (quenching (DQ)) was applied to some steel plates after rolling. With respect to other steel plates, air cooling was performed after rolling, and water cooling (quenching (RQ)) was performed after reheating.
On the obtained steel plates, the surface hardness measurement, the evaluation of abrasion resistant property, the base material toughness measurement, a T shape fillet weld cracking test (evaluation of delayed fracture resistant property), a synthetic heat-affected zone test and a toughness test of a weld of an actual weld joint were carried out in accordance with following manners. The acquired result is shown in Table 3.
The surface hardness measurement was carried out on each steel plate in accordance with the stipulation of JIS Z 2243 (1998) for measuring surface hardness below a surface layer (hardness of a surface measured after removing scales on the surface layer). In the measurement, tungsten hard balls having a diameter of 10 mm were used, and a load was set to 3000 kgf.
A V notch test specimen was sampled from each steel plate in the direction perpendicular to the rolling direction at a position away from a surface of the steel plate by ¼ of a plate thickness in accordance with the stipulation of JIS Z 2202 (1998), and a Charpy impact test was carried out at three respective temperatures with respect to each steel plate in accordance with the stipulation of JIS Z 2242 (1998), and absorbed energy at a test temperature of 0° C. was obtained, and base-material toughness is evaluated. The test temperature of 0° C. was selected by taking the use of the steel plate in a warm area into consideration.
The steel plate where an average of three absorbed energies (also referred to as vE0) at the test temperature of 0° C. was 30 J or more was determined as the steel plate having excellent base-material toughness (within the scope of the present invention).
With respect to abrasion resistant property, a rubber wheel abrasion test was carried out on each steel plate in accordance with the stipulation of ASTM G65. The test was carried out by using specimens each having a size of 10 mmt (t: plate thickness)×75 mmw (w: width)×20 mL (L: length) (t (plate thickness)×75 mmw×20 mL when the plate thickness is less than 10 mmt), and by using abrasive sands made of 100% SiO2 as an abrasive material.
A weight of the specimen was measured before and after the test, and wear of the specimen was measured. The test result was evaluated based on an abrasion resistance rate: (wear of soft steel plate)/(wear of each steel plate) using the wear of soft steel plate (SS400) as the reference (1.0). This means that the larger the abrasion resistance rate, the more excellent the abrasion resistant property becomes, and with respect to the scope of the present invention, the steel plate which exhibited the abrasion resistance rate of 4.0 or more was determined excellent.
In a T shape fillet weld cracking test, restriction welding was carried out on specimens each of which was assembled in a T shape as shown in
The welding method was shielded metal arc welding (welding material: LB52UL (4.0 mmΦ)), wherein a heat input was 17 kJ/cm, and welding of 3 layers and 6 passes was carried out. After welding, the specimen was left at a room temperature for 48 hours and, thereafter, 5 pieces of weld cross-sectional observation samples (bead length 200 mm being equally divided by 5) were sampled from the test plate, and the presence or non-presence of occurrence of cracks in a welded heat affected zone was investigated by a projector and an optical microscope. In both the specimens prepared without preheating and the specimens prepared with preheating at a temperature of 100° C., in 5 respective sampled cross-sectional samples, the samples where the occurrence of cracks in the welded heat affected zone was not found at all were evaluated as being excellent in delayed fracture resistance.
In a synthetic heat-affected zone test, a bond area and a low-temperature tempering embrittlement area when one pass CO2 gas shielded arc welding with a welding heat input of 17 kJ/cm is performed were simulated. In the simulation of the bond area, the bond area was held at 1400° C. for 1 second and was cooled at a cooling rate of 30° C./s from 800 to 200° C. On the other hand, in the simulation of the low-temperature tempering embrittlement area, the low-temperature tempering embrittlement area was held at a temperature of 300° C. for 1 second and was cooled at a cooling rate of 5° C./s from 300 to 100° C.
A square bar test specimen sampled in the rolling direction was subjected to the above-mentioned heat cycle by a high-frequency induction heating device and, thereafter, a V notch Charpy impact test was carried out in accordance with the stipulation of JIS Z 2242 (1998). The V notch Charpy impact test was carried out with respect to three specimens for each steel plate while setting a test temperature at 0° C.
The steel plate where an average value of three absorbed energies (vE0) in the bond area and the low-temperature tempering embrittlement area was 30 J or more was determined as the steel plate having excellent weld toughness (within the scope of the present invention).
Further, to confirm toughness of an actual weld joint, bead on plate welding was applied to a steel plate by shielded metal arc welding (heat input: 17 kJ/cm, preheating: 150° C., welding material: LB52UL (4.0 mmΦ)). A Charpy impact specimen was sampled from a position 1 mm below a surface of the steel plate, and a V notch Charpy impact test was carried out in accordance with the stipulation of JIS Z 2242 (1998) using a notch location as the bond area.
The V notch Charpy impact test of the actual weld joint was carried out using three specimens for each test temperature while setting the test temperature at 0° C. The steel plate where an average value of three absorbed energies (vE0) is 30 J or more was determined as the steel plate having excellent bond area toughness (within the scope of the present invention).
Table 2 shows manufacturing conditions of steel plates used in the test, and Table 3 shows the results of the above-mentioned respective tests. The present invention examples (steels No. 1 to 5) had the surface hardness of 400 HBW10/3000 or more, exhibited excellent abrasion resistant property, and had base-material toughness of 30 J or more at 0° C. Further, no cracks occurred in the T shape fillet weld cracking test, and the present invention examples had excellent toughness also with respect to the synthetic heat-affected zone test and the actual weld and hence, it was confirmed that the present invention examples exhibited excellent weld toughness.
On the other hand, with respect to comparison examples (steels No. 6 to 14) whose compositions were outside the scope of the present invention, it was confirmed that the comparison examples could not satisfy targeted performances with respect to any one or a plurality of properties and tests among surface hardness, abrasion resistant property, the T shape fillet weld cracking test, base-material toughness, the reproduced heat cycle Charpy impact test, the Charpy impact test of the actual weld joint.
Steel slabs which were prepared with various compositions shown in Table 4 by way of a steel converter, ladle refining and a continuous casting method were heated at a temperature of 1000 to 1250° C. and, thereafter, the steel slabs were subjected to hot rolling under manufacturing conditions shown in Table 5. Water cooling (quenching (DQ)) is applied to some steel plates immediately after rolling. With respect to other steel plates, air cooling was applied to other steel plates after rolling, and water cooling (quenching (RQ)) was performed after reheating.
On the obtained steel plates, the surface hardness measurement, the evaluation of abrasion resistant property, the base material toughness measurement, a T shape fillet weld cracking test (evaluation of delayed fracture resistant property), a synthetic heat-affected zone test and a toughness test of a weld of an actual weld joint were carried out in accordance with following manners. The acquired result is shown in Table 6.
The surface hardness measurement was carried out in accordance with the stipulation of JIS Z 2243 (1998) thus measuring surface hardness below a surface layer (hardness of a surface measured after removing scales on the surface layer). In the measurement, tungsten hard balls having a diameter of 10 mm were used, and a load was set to 3000 kgf.
A V notch test specimen was sampled from each steel plate in the direction perpendicular to the rolling direction at a position away from a surface of the steel plate by ¼ of a plate thickness in accordance with the stipulation of JIS Z 2202 (1998), and a Charpy impact test was carried out at three respective temperatures with respect to each steel plate in accordance with the stipulation of JIS Z 2242 (1998), and absorbed energy at test temperatures of 0° C. and −40° C. were obtained, and base-material toughness was evaluated. The test temperature of 0° C. was selected by taking the use of the steel plate in a warm region into consideration, and the test temperature of −40° C. was selected by taking the use of the steel plate in a cold region into consideration.
The steel plate where an average value of three absorbed energies (also referred to as vE0) at the test temperature of 0° C. was 30 J or more and an average value of three absorbed energies (also referred to as vE−40) at the test temperature of −40° C. was 27 J or more was determined as the steel plate having excellent base-material toughness (within the scope of the present invention). With respect to the steel plates having a plate thickness of less than 10 mm, V notch Charpy specimens having a sub size (5 mm×10 mm) were sampled and were subjected to a Charpy impact test. The steel plate where an average value of three absorbed energies (vE0) was 15 J or more and an average value of three absorbed energies (vE−40) was 13 J or more was determined as the steel plate having excellent base-material toughness (within the scope of the present invention).
With respect to abrasion resistant property, a rubber wheel abrasion test was carried out in accordance with the stipulation of ASTM G65. The test was carried out by using a specimen having a size of 10 mmt (t: plate thickness)×75 mmw (w: width)×20 mL (L: length) (t (plate thickness)×75 mmw×20 mL when the plate thickness was less than 10 mmt), and by using abrasive sand made of 100% SiO2 as an abrasive material.
A weight of the specimen was measured before and after the test and wear of the specimen was measured. The test result was evaluated based on an abrasion resistance rate: (wear of soft steel plate)/(wear of each steel plate) using wear of soft steel plate (SS400) as the reference (1.0). This means that the larger the abrasion resistance rate, the more excellent the abrasion resistant property becomes, and with respect to the scope of the present invention, the steel plate which exhibits the abrasion resistance rate of 4.0 or more was determined excellent.
In a T shape fillet weld cracking test, restriction welding was carried out on a specimen which was assembled in a T shape as shown in
The welding method was shielded metal arc welding (welding material: LB52UL (4.0 mmΦ)), wherein a heat input was 17 kJ/cm, and welding of 3 layers and 6 passes was carried out. After the test, the specimen was left at a room temperature for 48 hours and, thereafter, 5 pieces of weld cross-sectional observation samples (bead length 200 mm being equally divided by 5) were sampled from a test plate, and the presence or non-presence of occurrence of cracks in a welded heat affected zone was investigated by a projector and an optical microscope. In both the specimens prepared without preheating and the specimens prepared with preheating at a temperature of 100° C., among 5 respective sampled cross-sectional samples, the samples where the occurrence of cracks in the welded heat affected zone was not found at all were evaluated as being excellent in delayed fracture resistance.
In a synthetic heat-affected zone test, a bond area and a low-temperature tempering embrittlement area when one pass CO2 gas shielded arc welding with a welding heat input of 17 kJ/cm is performed were simulated. In the simulation of the bond area, the bond area was heated at 1400° C. for 1 second and was cooled at a cooling rate of 30° C./s from 800 to 200° C. Further, in the simulation of the low-temperature tempering embrittlement area, the low-temperature tempering embrittlement area was heated at a temperature of 300° C. for 1 second and was performed at a cooling rate of 5° C./s from 300 to 100° C.
A square bar test specimen sampled in the rolling direction was subjected to the above-mentioned heat cycle by a high-frequency induction heating device and, thereafter, a V notch Charpy impact test was carried out in accordance with the stipulation of JIS Z 2242 (1998). The V notch Charpy impact test was carried out with respect to three specimens for each steel plate while setting test temperatures at 0° C. and −40° C. at respective temperatures.
The steel plate where an average value of three absorbed energies (vE0) in the bond area and the low-temperature tempering embrittlement area was 30 J or more and an average value of three absorbed energies (vE−40) in the bond area and the low-temperature tempering embrittlement area was 27 J or more was determined as the steel plate having excellent weld toughness (within the scope of the present invention).
With respect to the steel plates having a plate thickness of less than 10 mm, V notch Charpy specimens having a sub size (5 mm×10 mm) were sampled and were subjected to a Charpy impact test. The steel plate where an average value of three absorbed energies (vE0) was 15 J or more in the bond area and the low-temperature tempering embrittlement area and an average value of three absorbed energies (vE−40) was 13 J or more in the bond area and the low-temperature tempering embrittlement area was determined as the steel plate having excellent weld toughness (within the scope of the present invention).
Further, to confirm toughness of an actual weld joint, bead on plate welding was applied to a steel plate by shielded metal arc welding (heat input: 17 kJ/cm, preheating: 150° C., welding material: LB52UL (4.0 mmΦ)). A Charpy impact specimen was sampled from a position 1 mm below a surface of the steel plate, and a V notch Charpy impact test was carried out in accordance with the stipulation of JIS Z 2242 (1998) using a notch location as the bond area.
The V notch Charpy impact test of the actual weld joint was carried out using three specimens for each test temperature while setting the test temperatures at 0° C. and −40° C. The steel plate where an average value of three absorbed energies (vE0) is 30 J or more and an average value of three absorbed energies (vE−40) is 27 J or more was determined as the steel plate having excellent bond area toughness (within the scope of the present invention).
With respect to the steel plates having a plate thickness of less than 10 mm, V notch Charpy specimens having a sub size (5 mm×10 mm) were sampled and were subjected to a Charpy impact test. The steel plate where an average value of three absorbed energies (vE0) was 15 J or more and an average value of three absorbed energies (vE−40) was 13 J or more was determined as the steel plate having excellent bond area toughness (within the scope of the present invention).
Table 5 shows manufacturing conditions of steel plates used in the test, and Table 6 shows the results of the above-mentioned respective tests. The present invention examples (steels No. 15 to 17 (steel No. 17 having a plate thickness of 8 mm)) had the surface hardness of 400 HBW10/3000 or more, exhibited excellent abrasion resistant property, and had base-material toughness of 30 J or more at 0° C. and base-material toughness of 27 J or more at −40° C. Further, no cracks occurred in the T shape fillet weld cracking test, and the present invention examples also had excellent toughness with respect to the synthetic heat-affected zone test and the actual weld and hence, it was confirmed that the present invention examples exhibited excellent weld toughness.
On the other hand, it was confirmed that although the steel No. 18 where the composition falls within the scope of the present invention but DI* exceeds 180 exhibited favorable results in surface hardness, abrasion resistant property, base-material toughness and a T shape fillet weld cracking test, the results of a reproduced heat cycle Charpy impact test corresponding to the low-temperature tempering embrittlement area and an actual weld joint Charpy impact test were close to lower limit values of targeted performances and hence, the steel No. 18 was inferior to other present invention examples with respect to low-temperature weld toughness.
The steel No. 19 fell outside the range of the present invention with respect to Si in composition. Accordingly, although the steel No. 19 exhibited the favorable results in surface hardness, abrasion resistant property and base-material toughness, toughness in the tempering embrittlement area of the welded heat affected zone were deteriorated and hence, the steel No. 19 could not satisfy the targeted performances with respect to a T shape fillet weld cracking test, a synthetic heat-affected zone Charpy impact test corresponding to the low-temperature tempering embrittlement area and an actual weld joint Charpy impact test.
Although the steel No. 20 falls within the scope of the present invention in composition, a value obtained by the formula (2) exceeded 0.47. Accordingly, it was confirmed that vE−40 is close to a lower limit of the performance of the present invention in both a synthetic heat-affected zone Charpy impact test and an actual weld joint Charpy impact test so that the steel No. 20 is inferior to other present invention examples. In the description of Tables 4, 5 and 6, although the steels No. 18 and 20 fall within the scope of the present invention called for in claim 3 in composition, the value of DI* and the value of the formula (2) fall outside the scope of the present invention called for in claims 6, 7 and hence, these steels are set as comparison examples.
0.16
0.321
1.43
0.013
0.14
0.001
0.039
0.001
0.55
0.48
33.1
6
7
8
9
10
11
12
13
14
3.0
14
cracks occurred
cracks occurred
23
cracks occurred
cracks occurred
cracks occurred
cracks occurred
28
15
29
25
cracks occurred
cracks occurred
20
11
21
17
21
23
14
10
19
3.5
18
19
20
24
cracks
cracks
23
21
28
14
occurred
occurred
| Number | Date | Country | Kind |
|---|---|---|---|
| 2010-149649 | Jun 2010 | JP | national |
| 2011-142506 | Jun 2011 | JP | national |
| Filing Document | Filing Date | Country | Kind | 371c Date |
|---|---|---|---|---|
| PCT/JP2011/065416 | 6/29/2011 | WO | 00 | 2/21/2013 |
