WO2014020891A1 - 耐摩耗鋼板およびその製造方法 - Google Patents
耐摩耗鋼板およびその製造方法 Download PDFInfo
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Definitions
- the present invention is suitable for use in construction machinery, shipbuilding, steel pipes, civil engineering, construction, etc., and is a wear resistant steel sheet having a plate thickness of more than 30 mm and not more than 150 mm.
- the present invention relates to a steel plate excellent in impact wear resistance when exposed and a method for producing the same.
- the wear-resistant steel increases the hardness of the martensite structure itself by increasing the amount of dissolved C in order to improve the wear resistance by using a microstructure as a martensite single phase structure.
- the low-temperature cracking sensitivity and toughness of the steel sheet are inferior. Therefore, wear-resistant steel with improved low temperature toughness and toughness has been developed.
- Patent Document 1 relates to a thick, high hardness, high toughness wear-resistant steel and a method for producing the same, and 0.20 to 0.40% C-Si-Mn-low so that uniform high hardness and high toughness can be obtained in the thickness direction.
- Re-harden steel with P-Nb-B composition and containing one or more of Cu, Ni, Cr, Mo, V, Ti, Ca and REM It is described that the martensite main structure is 6 or more in ASTM austenite grain size.
- Patent Document 2 has a 0.15 to 0.30% C-Si-Mn-low P, S-Nb composition in order to ensure wear resistance and workability in a low temperature range, with respect to the wear-resistant steel sheet and its manufacturing method.
- the composition satisfies the parameter formula consisting of one or more elements of Cu, Ni, Cr, Mo, V, Ti and B, and reduces the hardness difference between the steel sheet surface layer and the interior, and at -40 ° C Charpy It describes that the absorbed energy is 27 J or more.
- Patent Document 3 relates to a wear-resistant steel sheet having excellent low-temperature toughness and a method for producing the same, having a 0.23-0.35% C—Si—Mn—low P, S—Nb—Ti—B composition, Cu, Ni, Steel having a composition satisfying the parameter formula consisting of one or more elements of Cr, Mo and V is re-heated and hardened, and the microstructure is a martensite-based structure with a particle size of 15 ⁇ m or less. It describes that Charpy absorbed energy at 20 ° C. is 27 J or more.
- Patent Document 4 relates to a wear-resistant steel sheet having excellent low-temperature toughness and a method for producing the same, and has a composition of 0.23 to 0.35% C—Si—Mn—low P, S—Cr—Mo—Nb—Ti—B—REM system. Then, after rolling a steel having a composition satisfying the parameter formula consisting of one or more elements of Cu, Ni and V, and directly quenching, the microstructure is a martensitic main structure having a grain size of 25 ⁇ m or less, It describes that the wear resistance and Charpy absorbed energy at ⁇ 20 ° C. are 27 J or more.
- impact wear resistance may be required.
- Abrasion is a phenomenon in which a surface layer portion of steel material is scraped off by continuous contact between steel materials or different materials such as rocks in a working part such as a machine or an apparatus.
- impact wear is an environment in which dissimilar materials of high hardness collide with high loads, such as when steel is used for the liner material of a ball mill, and the impact surface on the steel material side undergoes repeated plastic deformation.
- the impact resistance of steel is inferior, it may not only cause failure of the machine and equipment, but also there is a risk that the strength of the structure cannot be maintained. Therefore, frequent repair and replacement of wear parts is inevitable. It is. For this reason, the request
- part which wears in an impact environment is strong.
- the impact-resistant wear characteristic is often required by a machine, an apparatus, etc., it is required to be provided at the surface layer portion and the cross-sectional portion of the steel plate.
- Patent Document 1 does not consider the wear resistance performance in the case of receiving an impact load.
- the central portion of the plate thickness has a reduced impact wear resistance due to the generation of a white layer having a high C martensite structure. There is concern about the occurrence of brittle fracture.
- Patent Document 2 does not consider the wear resistance performance in the case of receiving an impact load, and has not yet improved the impact wear characteristics of the surface layer portion and the cross-section portion of the steel plate.
- Patent Documents 3 and 4 also do not describe the wear resistance performance in the case of receiving an impact load.
- a high-C martensite structure reduces the impact wear resistance and brittle fracture due to the formation of a white layer. It is inevitable to occur.
- the impact wear characteristics are often required when used in machines, devices, and the like, and therefore are required to be provided in the surface layer portion and the cross-sectional portion of the steel sheet.
- an object of the present invention is to provide a wear-resistant steel sheet having excellent impact wear characteristics at the surface layer and cross-section of the steel sheet and a method for producing the same.
- the surface layer portion refers to a portion from the steel surface to a depth of 1 mm.
- the inventors of the present invention have made it possible to obtain excellent impact-resistant wear characteristics in both the surface layer portion and the cross-sectional portion of the steel sheet, and to obtain excellent toughness as a steel sheet. As a result of earnest research on various factors that determine the manufacturing method and microstructure, the following findings were obtained.
- the steel plate surface layer portion preferably has a 100% martensite structure, but a martensite structure having an area fraction of 90% or more is sufficient.
- Other than martensite may include lower bainite, upper bainite, cementite, pearlite, ferrite, retained austenite, or carbides such as Mo, Ti, and Cr. If the area fraction is 10% or less and the Brinell hardness of the surface layer portion can ensure 450HBW10 / 3000 or more, sufficient impact wear resistance can be obtained.
- the center portion of the plate thickness refers to a region of up to 0.5 mm in the front and back direction with respect to the 1/2 position of the plate thickness.
- the present invention has been made by further studying the obtained knowledge. That is, the present invention 1. In mass%, C: 0.25 to 0.33%, Si: 0.1 to 1.0%, Mn: 0.40 to 1.3%, P: 0.010% or less, S: 0.004% or less, Al: 0.06% or less, and N: 0.007% or less Furthermore, Cu: 1.5% or less, Ni: 2.0% or less, Cr: 3.0% or less, Mo: 1.5% or less, W: 1.5% or less and B: 0.0030% or less , (1) DI * is 100 to 250, and the balance has a steel composition consisting of Fe and inevitable impurities, The surface layer portion corresponding to the part from the steel plate surface to a depth of 1 mm has martensite of 90% or more in area fraction, the Brinell hardness of the steel plate surface is 450HBW10 / 3000 or more, and is 1/2 of the plate thickness of the steel plate A wear-resistant steel sheet comprising lower bainite having an average crystal grain size of 25 ⁇ m or less with an area fraction of 70%
- 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)
- Each element symbol is content (mass%)
- the steel slab having the steel composition described in any one of 1 to 3 above is heated to 1000 ° C. to 1200 ° C., hot-rolled and air-cooled to room temperature, and then the obtained steel plate is heated to Ac 3 to 950 ° C.
- a steel slab having the steel composition described in any one of 1 to 3 above is heated to 1000 ° C. to 1200 ° C., and hot-rolled in a temperature range of Ar 3 or higher, and the obtained steel sheet is converted to Ar 3 to 950.
- a wear-resistant steel sheet having excellent impact wear resistance at the surface layer and the cross-section can be obtained, which greatly contributes to the improvement of manufacturing efficiency and safety at the time of steel structure production, and has a remarkable industrial effect. Play.
- the component composition and the microstructure are defined.
- “Ingredient composition] In the following description,% is mass%.
- the content exceeds 0.33%, not only the weldability is deteriorated, but also when a shocking repeated load is applied, a white layer is likely to be formed, and the occurrence of wear and cracks due to peeling is promoted, resulting in resistance to damage. Impact wear characteristics deteriorate. For this reason, it is limited to the range of 0.25 to 0.33%.
- the content is 0.26 to 0.31%.
- Si acts as a deoxidizer and is not only necessary for steelmaking, but also has an effect of increasing the hardness of the steel sheet by solid solution and solid solution strengthening. In order to obtain such an effect, the content of 0.1% or more is required. On the other hand, if the content exceeds 1.0%, the weldability and toughness deteriorate significantly, so the content is limited to the range of 0.1 to 1.0%. Preferably, it is 0.2 to 0.8%.
- Mn 0.40 to 1.3%
- Mn has the effect of increasing the hardenability of the steel, and 0.40% or more is necessary to ensure the hardness of the base material.
- Mn is contained exceeding 1.3%, not only the toughness, ductility and weldability of the base metal are deteriorated, but also the grain boundary segregation of P is promoted at the central segregation portion, and the occurrence of delayed fracture is promoted.
- the amount of MnS generated in the central part of the plate thickness increases and becomes coarse, and when the cross section of the steel plate is exposed to a shocking wear environment, stress concentrates near the MnS and promotes the formation of a white layer. As a result, the impact wear resistance deteriorates. For this reason, it is limited to a range of 0.40 to 1.3%. Preferably, it is 0.50 to 1.2%.
- P 0.010% or less
- P When P is contained in excess of 0.010%, it segregates at the grain boundary, becomes the starting point of delayed fracture, and deteriorates toughness. For this reason, 0.010% is made the upper limit of the content, and it is desirable to reduce it as much as possible. In addition, excessive P reduction raises the refining cost and is economically disadvantageous, so it is desirable to make it 0.002% or more.
- S 0.004% or less S not only deteriorates the low-temperature toughness and ductility of the base metal, but also increases as the amount of MnS generated in the center of the plate increases and the cross-section of the steel plate becomes a shocking wear environment. When exposed, stress concentrates in the vicinity of MnS, the formation of a white layer is promoted, and the impact wear resistance deteriorates. For this reason, it is desirable to reduce 0.004% as an upper limit.
- Al acts as a deoxidizer and is most commonly used in the molten steel deoxidation process of steel sheets.
- it has the effect of suppressing coarsening of crystal grains, and also has the effect of suppressing toughness degradation and delayed fracture due to reduction of solid solution N .
- Al exceeds 0.06%, the amount of AlN and Al 2 O 3 generated in the central part of the plate thickness increases and becomes coarse, and the steel plate cross-section is exposed to a shocking wear environment. , Stress concentrates in the vicinity of AlN and Al 2 O 3 , the formation of a white layer is promoted, and the impact wear resistance deteriorates. For this reason, it is limited to 0.06% or less.
- N 0.007% or less N is contained in steel as an unavoidable impurity. If it exceeds 0.007%, the amount of AlN generated in the center of the plate increases and becomes coarse, and the cross section of the steel plate is shocking. When exposed to a wear environment, stress concentrates in the vicinity of AlN, the formation of a white layer is promoted, and the impact wear resistance deteriorates. For this reason, it is limited to 0.007% or less.
- Cu, Ni, Cr, Mo, W, and B are all elements that improve hardenability and contribute to improving the hardness of steel. , Depending on the desired strength.
- the content is preferably 0.05% or more. However, if it exceeds 1.5%, hot brittleness is caused to deteriorate the surface properties of the steel sheet, so the content is made 1.5% or less.
- Ni is added, the content is preferably 0.05% or more. However, if it exceeds 2.0%, the effect is saturated and economically disadvantageous, so the content is made 2.0% or less.
- Cr is added, the content is preferably 0.05% or more.
- the content is made 3.0% or less.
- Mo is an element that significantly increases the hardenability and is effective in increasing the hardness of the base material. In order to obtain such an effect, the content is preferably 0.05% or more. However, if it exceeds 1.5%, the base material toughness, ductility and weld crack resistance are adversely affected.
- W is an element that significantly increases the hardenability and is effective in increasing the hardness of the base material. In order to obtain such an effect, the content is preferably 0.05% or more. However, if it exceeds 1.5%, the base material toughness, ductility and weld crack resistance are adversely affected. .
- the content is preferably 0.0003% or more. However, if it exceeds 0.0030%, the base material toughness, ductility and weld crack resistance are adversely affected. .
- 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): 100-250 DI * is specified to have excellent wear resistance with 90% or more of the surface layer of the base material being martensite and the structure of the central part of the thickness being the lower bainite with an area fraction of 70% or more. , DI * value is 100-250.
- the range is 100 to 250.
- a range of 120 to 230 is preferable.
- the above is the basic component composition of the present invention, with the balance being Fe and inevitable impurities.
- Nb 0.005-0.025%
- Nb is an element that precipitates as carbonitride, refines the microstructure, fixes solute N, and has the effect of improving toughness and suppressing the occurrence of delayed fracture.
- a content of 0.005% or more is necessary.
- the content exceeds 0.025%, coarse carbonitride precipitates, the formation of a white layer is promoted, and the impact wear resistance deteriorates. For this reason, it is limited to a range of 0.005 to 0.025%.
- V 0.01 to 0.1%
- V is an element that precipitates as carbonitride, refines the microstructure, fixes solute N, and has the effect of improving toughness and suppressing the occurrence of delayed fracture.
- a content of 0.01% or more is necessary.
- the content exceeds 0.1%, coarse carbonitride precipitates, promotes the formation of a white layer, and deteriorates the impact wear resistance. For this reason, it is limited to a range of 0.01 to 0.1%.
- Ti has the effect of suppressing coarsening of crystal grains by fixing solid solution N to form TiN, and also has the effect of suppressing toughness deterioration and delayed fracture due to reduction of solid solution N. In order to obtain these effects, a content of 0.005% or more is necessary. On the other hand, if the content exceeds 0.03%, coarse carbonitride precipitates, the formation of a white layer is promoted, and the impact wear resistance deteriorates. For this reason, it is limited to a range of 0.005 to 0.03%.
- REM, Ca, and Mg all contribute to the improvement of toughness, and are selected and added according to desired characteristics.
- the content is preferably 0.002% or more, but the effect is saturated even if it exceeds 0.02%, so 0.02% is made the upper limit.
- the content is preferably set to 0.0005% or more. However, if the content exceeds 0.005%, the effect is saturated, so 0.005% is made the upper limit.
- the content is preferably 0.001% or more. However, if the content exceeds 0.005%, the effect is saturated, so 0.005% is made the upper limit.
- the microstructure of the steel sheet in the central part of the sheet thickness which is a portion from the 1/2 position of the steel sheet thickness to 0.5 mm in the front and back direction
- Lower bainite having an average crystal grain size of equivalent circle diameter of 25 ⁇ m or less has an area fraction of 70% or more.
- the average crystal grain diameter exceeds 25 ⁇ m in terms of equivalent circle diameter, toughness is reduced and delayed fracture occurs.
- martensite is included as a structure other than the lower bainite, the formation of a white layer is promoted through the presence of non-metallic inclusions and the like, and crack generation and impact wear resistance deteriorate.
- the effect is negligible if it is less than%. Furthermore, when upper bainite, ferrite, pearlite, and the like are present, the hardness is lowered and the impact wear resistance is deteriorated. However, the effect is negligible if it is 20% or less.
- the surface layer portion corresponding to a portion from the steel surface to a depth of 1 mm has a martensite structure with an area fraction of 90% or more from the viewpoint of impact resistance. Excellent impact wear resistance can be ensured by using a martensite structure of 90% or more and a steel sheet surface hardness of 450HBW10 / 3000 or more in terms of Brinell hardness.
- the microstructure observation method will be described in detail in Examples.
- the surface hardness of the steel plate is less than 450HBW10 / 3000 in Brinell hardness, the impact wear resistance is not sufficient and the life as a wear resistant steel is shortened. Therefore, the surface hardness is set to 450HBW10 / 3000 or more in terms of Brinell hardness.
- the wear-resistant steel according to the present invention can be manufactured under the following manufacturing conditions.
- the “° C.” display relating to the temperature means the temperature at the 1/2 position of the plate thickness.
- the molten steel having the above composition is melted by a known melting method, and a steel material such as a slab having a predetermined size is obtained by, for example, a continuous casting method or an ingot-bundling rolling method.
- the obtained steel material is cooled, immediately after casting, or once cooled and then reheated to 1000 to 1200 ° C., and then hot rolled to obtain a steel plate having a desired thickness. If the reheating temperature is less than 1000 ° C, the deformation resistance in hot rolling becomes high and the amount of reduction per pass cannot be made large, so the number of rolling passes increases and the rolling efficiency decreases, and the steel material
- the casting defect in (slab) may not be crimped.
- the reheating temperature of the steel material is set to a range of 1000 to 1200 ° C.
- the reheated steel material is hot-rolled until the desired thickness is reached.
- the hot rolling conditions are not particularly limited as long as the intended plate thickness and shape can be satisfied. However, in the case of an extremely thick steel plate having a plate thickness exceeding 70 mm, it is desirable to secure at least one or more rolling passes at which the rolling reduction per pass is 15% or more for zaku pressure bonding.
- the rolling end temperature is preferably Ar 3 or higher.
- the rolling resistance increases because the deformation resistance increases, the burden on the rolling mill increases, and in order to reduce the thick material to a rolling temperature of Ar 3 or less, It is necessary to wait in the middle of rolling, which greatly hinders productivity.
- the holding time is not particularly specified, but if it exceeds 1 hr, the toughness of the base material deteriorates due to the coarsening of austenite grains, so that it is preferably within 1 hr. If soaking in the heat treatment furnace is good, holding for a short time may be possible.
- the content value of each component of the steel material can be derived by using the relational expression defined by the element symbol (the element symbol represents the content (% by mass) of each element in the steel material).
- the content value of each component of the steel material can be derived by using the relational expression defined by the element symbol (the element symbol represents the content (% by mass) of each element in the steel material).
- Quenching may be performed by injecting a high-speed high-speed water stream onto the surface of the steel sheet, or by immersing the steel sheet in water.
- the cooling rate at the 1/2 position of the plate thickness is about 20 ° C / s when the plate thickness is 35mm, about 10 ° C / s when the plate thickness is 50mm, and 3 ° C / second when the plate thickness is 70mm. It is about s.
- the central part of the plate thickness can be made to have a structure in which the lower bainite has an area fraction of 70% or more.
- the plate thickness is 30 mm or less, if quenching is performed by water cooling, the cooling rate becomes too high, and the central portion of the plate thickness cannot have a structure with the lower bainite having an area fraction of 70% or more.
- the steel sheet after hot rolling and direct quenching may be further subjected to a reheating quenching process in which it is reheated to Ac 3 to 950 ° C.
- the structure in the thick steel plate is further homogenized and refined, and the strength and toughness of the base material are improved.
- a steel slab prepared with various components and compositions shown in Table 1 by the converter-ladle refining-continuous casting method was heated to 1000-1200 ° C under the conditions shown in Table 2, and then hot-rolled.
- the steel sheet of the part was directly quenched (DQ) immediately after rolling.
- DQ directly quenched
- RQ quenched
- RQ quenching
- the obtained steel sheet was subjected to structure observation, surface hardness measurement, base material toughness, and impact wear test in the following manner.
- Test specimens were collected from each steel plate, and the structure was observed with an optical microscope and a transmission electron microscope at a position corresponding to 1/2 of the thickness (t) in the thickness direction of the cross section parallel to the rolling direction.
- Lower bainite fraction) and average grain size of prior austenite grains were determined. Since lower bainite transforms from austenite without long-distance diffusion, the grain size of lower bainite is the same as the prior austenite grain size. Further, lower bainite and martensite can be distinguished from each other by the difference in the precipitation form of cementite using an optical microscope, and more specifically using a transmission electron microscope.
- the surface hardness measurement was based on JIS Z2243 (1998), and the surface hardness under the surface layer was measured.
- a tungsten hard ball having a diameter of 10 mm was used, and the load was 3000 kgf.
- V-notch test specimens were collected from the direction perpendicular to the rolling direction at 1/4 part of the thickness (t) of each steel sheet in accordance with the provisions of JIS Z 2202 (1998).
- JIS Z 2242 (1998 The Charpy impact test at each temperature was conducted on each steel sheet in accordance with the provisions of (year), the absorbed energy at 0 ° C. was obtained, and the base material toughness was evaluated. The average value of the three absorbed energy (vE 0 ) was 30 J or more, and the base metal toughness was excellent.
- test pieces of 10 mm ⁇ 25 mm ⁇ 75 mm were taken from 1/2 part of the plate thickness (t) of the steel plate surface and cross section as shown in FIG.
- the test steel and SS400 test piece are fixed to the rotor of the impact wear test equipment shown in Fig. 2, and after sealing with 1500cm 3 of 100% SiO 2 silica (average particle size 30mm) in the drum, the rotor rotational speed is 600rpm.
- the drum rotation speed was 45 rpm and the total rotor rotation speed was 10,000.
- the surface of the test piece after the completion of the test was observed with a projector, and a specimen having no crack of 3 mm or longer was considered to have excellent cracking properties.
- the present invention example has a surface hardness of 450 HBW 10/3000 or more, a base material toughness of 0 ° C. of 30 J or more, no cracking in the impact wear test, and a wear resistance ratio to SS400. It has 3.0 or more at the steel plate surface layer part and 2.5 or more at 1 / 2t cross section. On the other hand, it was confirmed that one or more of the surface hardness, the base metal toughness, the impact wear test, or a plurality of the comparative examples outside the scope of the present invention cannot satisfy the target performance.
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Abstract
Description
また、C量の高いマルテンサイト組織を有する鋼材が、衝撃的な繰返し荷重を受けた場合には、白色層と呼ばれる極めて硬質で脆いミクロ組織が形成される。その結果、鋼材の白色層部分が脆性的に剥離して、十分な耐衝撃摩耗性が得られず、更に靭性が低い場合は、白色層を起点に脆性破壊が発生するおそれがある。
また、特許文献2にも、衝撃荷重を受ける場合の耐摩耗性能に関して考慮されておらず、鋼板の表層部および断面部の耐衝撃摩耗特性を改善するには至っていない。特許文献3、4も衝撃荷重を受ける場合の耐摩耗性能に関して記載されておらず、特に、板厚中央部では高Cのマルテンサイト組織で、白色層生成による耐衝撃摩耗性の低下や脆性破壊の発生が不可避である。なお、耐衝撃摩耗特性は、機械、装置等の中で使用される際に要求されることが多いことから、鋼板の表層部および断面部で備えていることが要求される。
すなわち、本発明は、
1.mass%で、C:0.25~0.33%、Si:0.1~1.0%、Mn:0.40~1.3%、P:0.010%以下、S:0.004%以下、Al:0.06%以下およびN:0.007%以下を含有し、更に、Cu:1.5%以下、Ni:2.0%以下、Cr:3.0%以下、Mo:1.5%以下、W:1.5%以下およびB:0.0030%以下のうちの一種または二種以上を含有し、(1)式で示されるDI*が100~250であり、残部がFeおよび不可避的不純物からなる鋼組成を有し、
鋼板表面から深さ1mmまでの部位にあたる表層部が面積分率で90%以上のマルテンサイトを有し、該鋼板表面のブリネル硬度が450HBW10/3000以上であり、該鋼板の板厚の1/2位置から表裏方向にそれぞれ0.5mmまでの部位にあたる板厚中央部が面積分率で70%以上の平均結晶粒径25μm以下である下部ベイナイトを有することを特徴とする、耐摩耗鋼板。
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)
各元素記号は含有量(mass%)
[成分組成]
以下の説明において%はmass%とする。
C:0.25~0.33%
Cは、マルテンサイトの硬度を高め、また、焼入れ性を高めて板厚中央部において所定の組織として優れた耐摩耗性を確保するために重要な元素であり、その効果を得るため、0.25%以上の含有を必要とする。一方、0.33%を超えて含有すると溶接性が劣化するだけでなく、衝撃的な繰返し荷重を受けた場合には、白色層が生成しやすくなり、剥離による摩耗やき裂の発生が促進されて耐衝撃磨耗特性が劣化する。このため、0.25~0.33%の範囲に限定する。好ましくは、0.26~0.31%である。
Siは、脱酸材として作用し、製鋼上、必要であるだけでなく、鋼に固溶して固溶強化により鋼板を高硬度化する効果を有する。このような効果を得るためには、0.1%以上の含有を必要とする。一方、1.0%を超えて含有すると、溶接性および靱性が顕著に劣化するため、0.1~1.0%の範囲に限定する。好ましくは、0.2~0.8%である。
Mnは、鋼の焼入れ性を増加させる効果を有し、母材の硬度を確保するために0.40%以上は必要である。一方、1.3%を超えてMnを含有すると、母材の靭性、延性および溶接性が劣化するだけでなく、中心偏析部でPの粒界偏析を助長し、遅れ破壊の発生を助長する。さらに、板厚中央部に生成するMnSの量が増加するとともに粗大になり、鋼板断面部が衝撃的な摩耗環境に曝された場合に、MnS近傍に応力が集中し、白色層の生成が促進され、耐衝撃摩耗性が劣化する。このため、0.40~1.3%の範囲に限定する。好ましくは、0.50~1.2%である。
Pを、0.010%を超えて含有すると、粒界に偏析し、遅れ破壊の発生起点になるとともに、靱性を劣化させる。このため、0.010%を含有量の上限とし、可能なかぎり低減することが望ましい。なお、過度のP低減は精錬コストを高騰させ経済的に不利となるため、0.002%以上とすることが望ましい。
Sは、母材の低温靭性や延性を劣化させるだけでなく、板厚中央部に生成するMnSの量が増加するとともに粗大になり、鋼板断面部が衝撃的な摩耗環境に曝された場合に、MnS近傍に応力が集中し、白色層の生成が促進され、耐衝撃摩耗性が劣化する。このため、0.004%を上限として低減することが望ましい。
Alは、脱酸剤として作用し、鋼板の溶鋼脱酸プロセスにおいて、もっとも汎用的に使われる。また、鋼中の固溶Nを固定してAlNを形成することにより、結晶粒の粗大化を抑制する効果を有するとともに、固溶N低減による靱性劣化と遅れ破壊の発生を抑制する効果を有する。一方、0.06%を超えてAlを含有すると、板厚中央部に生成するAlNおよびAl2O3の量が増加するとともに粗大になり、鋼板断面部が衝撃的な摩耗環境に曝された場合に、AlNおよびAl2O3近傍に応力が集中し、白色層の生成が促進され、耐衝撃摩耗性が劣化する。このため、0.06%以下に限定する。
Nは不可避的不純物として鋼中に含まれ、0.007%を超えて含有すると、板厚中央部に生成するAlNの量が増加するとともに粗大になり、鋼板断面部が衝撃的な摩耗環境に曝された場合に、AlN近傍に応力が集中し、白色層の生成が促進され、耐衝撃摩耗性が劣化する。このため、0.007%以下に限定する。
Cu、Ni、Cr、Mo、WおよびBは、いずれも焼入れ性を向上し、鋼の硬度向上に寄与する元素であり、所望する強度に応じて適宜含有できる。
Cuを添加する場合は、含有量を0.05%以上とすることが好ましいが、1.5%を超えると熱間脆性を生じて鋼板の表面性状を劣化させるため、1.5%以下とする。
Niを添加する場合は、含有量を0.05%以上とすることが好ましいが、2.0%を超えると効果が飽和し、経済的に不利になるため、2.0%以下とする。
Crを添加する場合は、0.05%以上とすることが好ましいが、3.0%を超えると靭性および溶接性が低下するため、3.0%以下とする。
Moは、焼入れ性を顕著に増加させ、母材の高硬度化に有効な元素である。このような効果を得るためには、含有量を0.05%以上とすることが好ましいが、1.5%を超えると、母材靭性、延性および耐溶接割れ性に悪影響を及ぼすため、1.5%以下とする。
Wは、焼入れ性を顕著に増加させ、母材の高硬度化に有効な元素である。このような効果を得るためには、含有量を0.05%以上とすることが好ましいが、1.5%を超えると、母材靭性、延性および耐溶接割れ性に悪影響を及ぼすため、1.5%以下とする。
Bは、微量の添加で焼入れ性を顕著に増加させ、母材の高硬度化に有効な元素である。このような効果を得るためには、含有量を0.0003%以上とすることが好ましいが、0.0030%を超えると、母材靭性、延性および耐溶接割れ性に悪影響を及ぼすため、0.0030%以下とする。
DI*は母材の表層部の90%以上をマルテンサイトとし、また板厚中央部の組織を面積分率で70%以上の下部ベイナイトとし、優れた耐摩耗性を有するために規定するもので、DI*の値を100~250とする。100未満の場合、板厚表層からの焼入れ深さが浅くなり、板厚中央部において所望のミクロ組織が得られず耐摩耗鋼としての寿命が短くなる。一方、250を超えると、靭性や遅れ破壊特性が顕著に劣化する。このため、100~250の範囲とする。好ましくは、120~230の範囲とする。
Nb:0.005~0.025%
Nbは、炭窒化物として析出し、ミクロ組織を微細化するとともに、固溶Nを固定して、靱性改善と、遅れ破壊の発生抑制の効果を兼備する元素である。このような効果を得るためには、0.005%以上の含有量が必要である。一方、0.025%を超えて含有すると、粗大な炭窒化物が析出し、白色層の生成が促進され、耐衝撃摩耗性が劣化する。このため、0.005~0.025%の範囲に限定する。
Vは、炭窒化物として析出し、ミクロ組織を微細化するとともに、固溶Nを固定して、靱性改善と、遅れ破壊の発生抑制の効果を兼備する元素である。このような効果を得るためには、0.01%以上の含有量が必要である。一方、0.1%を超えて含有すると、粗大な炭窒化物が析出し、白色層の生成が促進され、耐衝撃摩耗性が劣化する。このため、0.01~0.1%の範囲に限定する。
Tiは、固溶Nを固定してTiNを形成することにより、結晶粒の粗大化を抑制する効果を有するとともに、固溶N低減による靱性劣化と遅れ破壊の発生を抑制する効果を有する。これらの効果を得るためには、0.005%以上の含有量が必要である。一方、0.03%を超えて含有すると、粗大な炭窒化物が析出し、白色層の生成が促進され、耐衝撃摩耗性が劣化する。このため、0.005~0.03%の範囲に限定する。
REMを添加する場合は、含有量を0.002%以上とすることが好ましいが、0.02%を超えても効果が飽和するため、0.02%を上限とする。
Caを添加する場合は、含有量を0.0005%以上とすることが好ましいが、0.005%を超えても効果が飽和するため、0.005%を上限とする。
Mgを添加する場合は、含有量を0.001%以上とすることが好ましいが、0.005%を超えても効果が飽和するため、0.005%を上限とする。
本発明では、断面部の耐衝撃摩耗特性を向上させるため、鋼板の板厚の1/2位置から表裏方向にそれぞれ0.5mmまでの部位である板厚中央部での鋼板のミクロ組織については、平均結晶粒径が円相当直径で25μm以下である下部ベイナイトを面積分率で70%以上有する。
ここで、平均結晶粒径が円相当直径で25μmを超えると、靭性の低下や遅れ破壊の発生を招く。また、下部ベイナイト以外の組織としてマルテンサイトが含まれると、非金属介在物などの存在を介して、白色層の生成を助長し、き裂の発生や、耐衝撃摩耗性が劣化するが、10%以下であればその影響は無視できる。さらに、上部ベイナイト、フェライト、パーライトなどが存在する場合には、硬度が低下し、耐衝撃摩耗性が劣化するが、20%以下であればその影響は無視できる。
鋼板の表面硬度がブリネル硬さで450HBW10/3000未満の場合には、耐衝撃摩耗特性が十分でなく、耐摩耗鋼としての寿命が短くなる。そのため、表面硬度をブリネル硬さで450HBW10/3000以上とする。
本発明に係る耐摩耗鋼は、以下の製造条件で製造することが可能である。
説明において、温度に関する「℃」表示は、板厚の1/2位置における温度を意味するものとする。
得られた鋼素材は、冷却することなく鋳造直後に、または、一旦、冷却した後に1000~1200℃に再加熱し、その後、熱間圧延して所望の板厚の鋼板とする。再加熱温度が1000℃未満では、熱間圧延での変形抵抗が高くなり、1パス当たりの圧下量が大きく取れなくなることから、圧延パス数が増加し、圧延能率の低下を招くとともに、鋼素材(スラブ)中の鋳造欠陥を圧着することができない場合がある。一方、再加熱温度が1200℃を超えると、加熱時のスケールによって表面疵が生じやすく、圧延後の手入れ負荷が増大する。このため、鋼素材の再加熱温度を1000~1200℃の範囲とする。
圧延終了後、再加熱焼入れ処理を行う場合は、Ac3~950℃に再加熱し、一定時間保持後、焼入れを行う。加熱温度が、950℃を超えると鋼板表面性状が劣化するとともに結晶粒が粗大化し、靭性および遅れ破壊特性が劣化する。
Ac3=854-180C+44Si-14Mn-17.8Ni-1.7Cr
(元素記号は鋼材中の各元素の含有量(質量%)を表す)で定義される関係式を用いて鋼材の各成分の含有値を入力して導くことができる。
Ar3(℃)は例えば、
Ar3=910-310C-80Mn-20Cu-15Cr-55Ni-80Mo
(元素記号は鋼材中の各元素の含有量(質量%)を表す)で定義される関係式を用いて鋼材の各成分の含有値を入力して導くことができる。
転炉-取鍋精錬-連続鋳造法で、表1に示す種々の成分組成に調製した鋼スラブを、表2に示す条件で、1000~1200℃に加熱した後、熱間圧延を施し、一部の鋼板には圧延直後に直接焼入れ(DQ)をした。直接焼入れ(DQ)した一部の鋼板について、900℃に再加熱後焼入れ(RQ)を行った。また、熱間圧延、冷却後の一部の鋼板については、900℃に再加熱後焼入れ(RQ)を行った。
各鋼板から試験片を採取し、圧延方向と平行方向断面の板厚方向の板厚(t)の1/2にあたる位置で、光学顕微鏡および透過型電子顕微鏡により組織を観察し、組織分率(下部ベイナイト分率)および旧オーステナイト粒(旧γ粒)の平均粒径を求めた。下部ベイナイトは長距離拡散を伴わずにオーステナイトから変態するため、下部ベイナイトの粒径は旧オーステナイト粒径と同じである。また、下部ベイナイトとマルテンサイトは、大まかには光学顕微鏡を用いて、詳細には透過型電子顕微鏡を用いてセメンタイトの析出形態の差異により判別可能である。
試験終了後の試験片の表面を投影機にて観察し、長さ3mm以上の割れがないものを、割れ性に優れるとした。さらに、試験前後での試験片重量の減少量を測定した。(SS400の試験片の重量減少量)/(対象材の試験片の重量減少量)を耐摩耗比とし、鋼板表層部で3.0以上、板厚(t)の1/2断面部で2.5以上を有しているものを耐衝撃摩耗特性に優れるものとした。
表3から、本発明例は、表面硬度が450HBW10/3000以上を有し、0℃の母材靭性が30J以上を有し、かつ衝撃摩耗試験で割れが発生せず、SS400に対する耐摩耗比が鋼板表層部で3.0以上、1/2t断面部で2.5以上を有している。
一方、本発明範囲外の比較例は、表面硬度、母材靭性、および衝撃摩耗試験のいずれか、あるいはその複数が目標性能を満足できないことが確認された。
Claims (6)
- mass%で、C:0.25~0.33%、Si:0.1~1.0%、Mn:0.40~1.3%、P:0.010%以下、S:0.004%以下、Al:0.06%以下およびN:0.007%以下を含有し、更に、Cu:1.5%以下、Ni:2.0%以下、Cr:3.0%以下、Mo:1.5%以下、W:1.5%以下およびB:0.0030%以下のうちの一種または二種以上を含有し、(1)式で示されるDI*が100~250であり、残部がFeおよび不可避的不純物からなる鋼組成を有し、
鋼板表面から深さ1mmまでの部位にあたる表層部が面積分率で90%以上のマルテンサイトを有し、該鋼板表面のブリネル硬度が450HBW10/3000以上であり、該鋼板の板厚の1/2位置から表裏方向にそれぞれ0.5mmまでの部位にあたる板厚中央部が面積分率で70%以上の平均結晶粒径25μm以下である下部ベイナイトを有することを特徴とする、耐摩耗鋼板。
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)
各元素記号は含有量(mass%) - 前記鋼組成は、更にmass%で、Nb:0.005~0.025%、V:0.01~0.1%およびTi:0.005~0.03%のうちの一種または二種以上を含有することを特徴とする請求項1に記載の耐摩耗鋼板。
- 前記鋼組成は、更にmass%で、REM:0.02%以下、Ca:0.005%以下、Mg:0.005%以下のうちの一種または二種以上を含有することを特徴とする請求項1または2に記載の耐摩耗鋼板。
- 請求項1ないし3のいずれか一項に記載の鋼組成を有する鋼片を1000℃~1200℃に加熱後、熱間圧延を行い、室温まで空冷し、その後、得られた鋼板をAc3~950℃に再加熱して焼入れを行うことを特徴とする耐摩耗鋼板の製造方法。
- 請求項1ないし3のいずれか一項に記載の鋼組成を有する鋼片を1000℃~1200℃に加熱後、Ar3以上の温度域で熱間圧延を行った後、得られた鋼板をAr3~950℃の温度から焼入れを行うことを特徴とする耐摩耗鋼板の製造方法。
- 前記焼入れ後、更に前記鋼板をAc3~950℃に再加熱して焼入れを行うことを特徴とする請求項5に記載の耐摩耗鋼板の製造方法。
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Publication number | Priority date | Publication date | Assignee | Title |
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CN106133171A (zh) * | 2014-03-31 | 2016-11-16 | 杰富意钢铁株式会社 | 厚钢板及其制造方法 |
EP3128032A4 (en) * | 2014-03-31 | 2017-02-08 | JFE Steel Corporation | Thick steel sheet and method for producing same |
AU2015242070B2 (en) * | 2014-03-31 | 2018-02-22 | Jfe Steel Corporation | Thick steel plate and method for manufacturing the same |
CN110760645A (zh) * | 2019-11-18 | 2020-02-07 | 运城学院 | 一种耐磨钢板的热处理工艺 |
Also Published As
Publication number | Publication date |
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WO2014020891A8 (ja) | 2015-01-15 |
US9738957B2 (en) | 2017-08-22 |
AU2013297928A1 (en) | 2015-01-29 |
CN104508166A (zh) | 2015-04-08 |
MX2015001232A (es) | 2015-04-10 |
EP2881482A4 (en) | 2015-10-21 |
JP2014025130A (ja) | 2014-02-06 |
JP5966730B2 (ja) | 2016-08-10 |
EP2881482A1 (en) | 2015-06-10 |
CN104508166B (zh) | 2016-12-07 |
EP2881482B1 (en) | 2019-07-24 |
US20150184270A1 (en) | 2015-07-02 |
AU2013297928B2 (en) | 2016-06-02 |
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