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    公开号:BR112013007560B1
    申请号:R112013007560
    申请日:2011-09-28
    公开日:2018-09-25
    发明作者:Tsutomu Takeda；Ryuichi Kobayashi
    申请人:Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.)；
    IPC主号:
    专利说明:

    (54) Title: WELDING ACCUMULATION MATERIAL, DEPOSITED METAL AND ELEMENT WITH DEPOSITED METAL (51) Int.CI .: B23K 35/30; B23K 9/04 (30) Unionist Priority: 09/30/2010 JP 2010-222861 (73) Holder (s): KABUSHIKI KAISHA ΚΟΒΕ SEIKO SHO (ΚΟΒΕ STEEL, LTD.) (72) Inventor (s): TSUTOMU TAKEDA; RYUICHI KOBAYASHI (85) National Phase Start Date: 03/28/2013
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    WELDING ACCUMULATION MATERIAL, DEPOSITED METAL AND ELEMENT WITH DEPOSITED METAL
    TECHNICAL FIELD [001] The present invention relates to a welding accumulation material (welding coating), a deposited metal and an element with the deposited metal, and more particularly to a welding accumulation material, a deposited metal and an element with the deposited metal, which are suitable for use in a processing device that requires both high corrosion resistance and abrasion resistance.
    BACKGROUND OF THE TECHNIQUE [002] In a processing apparatus, such as a sprayer or a reactor, there are some cases in which a target substance comprising a strong acid such as hydrochloric acid or sulfuric acid is treated with a corrosive acid medium. A treatment container to contain the target substance is manufactured by subjecting steel materials in general to welding. For this reason, an inner wall of the treatment container is susceptible to damage due to not only abrasive wear, but also corrosion by the target substance. It is, therefore, desirable to provide an internal wall (welding element), having corrosion resistance and abrasion resistance.
    [003] On the other hand, the following Patent Document 1 discloses a deposited metal produced by the welding accumulation (welding coating), in which it has resistance to oxidation and resistance to abrasion and high hardness exposures, at a temperature 600 ° C or more. The deposited metal comprises C: 0.5 to 3.0%, Si: 3.0
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    2/40
    at 7.0%, Cr: 25 to 45%; Mn: 0 to 10% and Ni: 0 to 13%, in which Following relationship is satisfied: Cr > -1.6 Si +37, and the remaining composition It consists in Fe and impurities
    unavoidable, and where the deposited metal has a metal microstructure in which small fibers in the form of pieces of carbide are precipitated finely and in large numbers. Patent Document 1 also discloses a welding build-up material for forming the deposited metal. The welding accumulation material comprises C: 0.5 to 3.0%,
    Si: 3.0 to 7.0%, Cr: 25 to 45%; Mn: 0 to 10% and Ni : 0 13%, in what the following relationship is satisfied : Cr> -1.6 Si +37, and the rest of composition It consists in Faith and impurities
    inevitable.
    LIST OF DOCUMENTS OF PREVIOUS TECHNIQUES [PATENT DOCUMENTS]
    Patent Document 1 : JP 11-226778Adeposited metal disclosed at the SUMMARY[004] GIVES INVENTIONAlthough the Document in Patent 1 displays high temperature in resistance The oxidation the high, high temperature in resistance abrasion and high temperature high hardness, resistance The corrosion against an acid strong a an
    lower temperature (eg room temperature) is unknown. In addition, this deposited metal exhibits extremely high hardness of 550 or more, in terms of Vickers hardness, which gives rise to concerns about aggressive abrasion when used for the inner wall of the treatment vessel.
    [005] The present invention has been made in view of such circumstances and an object of the same is to provide
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    3/40 a deposited metal having excellent resistance to corrosion and abrasion resistance, as well as hardness, at room temperature, with an element of the deposited metal, and an accumulation of welding material to form the deposited metal.
    [006] According to one aspect of the present invention, a welding buildup material is provided which contains C: 0.2 to 1.5% by weight, Si: 0.5 to 2% by weight, Mn: 0, 5 to 2 wt%, Cr: 20 to 40 wt%, Mo: 2 to 6 wt%, Ni: 0.5 to 6 wt%, V: 1 to 5 wt% and W: 0.5 at 5% by mass, with the rest being Fe and unavoidable impurities.
    [007] According to another aspect of the present invention, there is provided a deposited metal produced by the welding accumulation, which contains C: 0.2 to 1.5% by mass, Si: 0.5 to 2% by mass, Mn : 0.5 to 2% by weight, Cr: 20 to 40% by weight, Mo: 2 to 6% by weight, Ni: 0.5 to 6% by weight, V: 1 to 5% by weight and W: 0.5 to 5% by weight, with the remainder being Fe and unavoidable impurities.
    [008] In accordance with yet another aspect of the present invention, there is provided an element comprising a steel material that serves as a base metal, and an accumulation of welded deposited metal on a surface of the steel material, on which the deposited metal contains C: 0.2 to 1.5% by weight, Si: 0.5 to 2% by weight, Mn:
    0.5 to 2 wt%, Cr: 20 to 40 wt%, Mo: 2 to 6 wt%, Ni: 0.5 to 6 wt%, V: 1 to 5 wt% and W: 0 , 5 to 5% by weight, with the remainder being Fe and unavoidable impurities.
    [009] Objects, characteristics, aspects and advantages of the present invention will be evident from the
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    4/40 attached drawings and detailed description.
    BRIEF DESCRIPTION OF THE DRAWINGS [FIG. 1] FIG. 1 is a diagram illustrating a Rockwell hardness of deposited metals from examples and comparative examples.
    [FIG. 2] FIG. 2 is a diagram illustrating a Vickers hardness of the metals deposited from the examples and comparative examples.
    [FIG. 3] FIG. 3 is a conceptual diagram that illustrates a principle of a soil abrasion test.
    [FIG. 4] FIG. 4 is a graph illustrating a result of the evaluation of abrasion resistance (weight loss by abrasion) of some of the metals deposited in the examples and comparative examples.
    [FIG. 5] FIG. 5 is a graph illustrating a result of the evaluation of abrasion resistance (weight loss by abrasion) of some of the metals deposited in the examples and comparative examples.
    [FIG. 6] FIG. 6 is a graph illustrating a result of the evaluation of abrasion resistance (weight loss by abrasion) of some of the metals deposited in the examples and comparative examples.
    [FIG. 7] FIG. 7 is a graph that illustrates a result of the evaluation of the corrosion resistance (average corrosion rate) of some of the metals deposited in the examples and comparative examples.
    [FIG. 8] FIG. 8 is a graph that illustrates a result of the evaluation of the corrosion resistance (average corrosion rate) of some of the metals deposited in the examples and comparative examples.
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    5/40 [FIG. 9] FIG. 9 are representative photographs of sectional microstructures of some of the metals deposited in the examples and comparative examples, as a substitute for the drawings.
    [FIG. 10] FIG. 10 are representative photographs of sectional microstructures of some of the metals deposited in the examples and comparative examples, as a substitute for the drawings.
    [FIG. 11] FIG. 11 are representative photographs of sectional microstructures of some of the metals deposited in the examples and comparative examples, as a substitute for the drawings.
    DESCRIPTION OF THE MODALITIES [0010] With reference to the drawings, modalities of the present invention will now be specifically described. It should be understood that the present invention is not limited to the modalities in any way.
    [0011] [Welding accumulation material and deposited metals]
    A welding build-up material according to an embodiment of the first aspect of the present invention contains C: 0.2 to 1.5% by mass, Si: 0.5 to 2% by mass, Mn: 0.5 to 2% by weight, Cr: 20 to 40% by weight, Mo: 2 to 6% by weight, Ni: 0.5 to 6% by weight, V: 1 to 5% by weight and W: 0.5 to 5% by weight mass, with the rest being Fe and unavoidable impurities.
    [0012] A deposited metal according to an embodiment of the second aspect of the present invention is a deposited metal produced by the accumulation of welding. The deposited metal contains C: 0.2 to 1.5% by weight, Si: 0.5 to 2% by weight, Mn: 0.5 to 2% by weight, Cr: 20 to 40% by weight,
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    Mo: 2 to 6% by mass, Ni: 0.5 to 6% by mass, V: 1 to 5% by mass and W: 0.5 to 5% by mass, with the remainder being Fe and unavoidable impurities.
    [0013] The metal deposited according to this modality is formed by the welding accumulation of the welding accumulation material according to this modality for a base metal.
    [0014] The base metal is not particularly limited, as long as it is a metal material capable of allowing a deposited material to be formed on a surface of it by welding accumulation. For example, a material for forming a container for a sprayer, reactor or similar includes various stainless steels, S25C steel, SC49 steel and SS400 steel.
    [0015] Gem accumulation conditions for forming the deposited metal according to this modality can be in conventional welding accumulation conditions. A deposited metal having a metal microstructure mentioned later (where the matrix comprises a plurality of ferrite grains and a plurality of cementite grains are precipitated from ferrite grain boundaries) can be obtained by conducting a weld pool under conventional conditions using the welding build-up material according to this modality. In this regard, it is desirable to heat the base metal during welding. More specifically, it is desirable to heat and cool the base metal at a temperature rise rate of 100 to 300 ° C / h, a holding temperature of 250 to 350 ° C and a cooling speed of 15 to 100 ° C / h, and carry out welding under the condition that the base metal is
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    7/40 isothermally carried out at a temperature of 250 to 350 ° C.
    [0016] The reasons why the components of the welding accumulation material and metals deposited in accordance with the above modalities are defined as above, will be described below.
    C: 0.2 to 1.5% by weight [0017] C (carbon) is an element that is effective in maintaining a balance between the strength of the tension and the elongation in each deposited metal, and a weld metal comprising the deposited metal and a molten base metal. In addition, C is an element that is effective in causing cementite (Fe3C) to be precipitated, in such a way as to wrap around ferrite grains to boundary grains in a ferrite matrix, during a cooling process, after the process welding accumulation. The C content (C quantity) is less than or equal to 1.5% by mass. This is because, if the quantity C is greater than 1.5% by mass, the fragility occurs due to the deterioration of the hardness, so that, in the treatment container, a tendency towards an increase of aggressive abrasion becomes prominent. Preferably, it is 0.8% or less by weight. This is because, when the amount C is equal to or less than 0.8% by mass, a deposited metal is formed as eutetoid steel or hypoeutetoid steel, which provides increased resistance and allows easier work. At the same time, the quantity C is equal to or greater than 0.2% by mass. This is because, if the quantity C is less than 0.2% by mass, with a thickness of a ferrite phase to be precipitated in the limit grains in the ferrite matrix, it becomes Petition 870180058798, of 06/07/2018, p. 14/51
    8/40 if smaller, so that a tendency to become difficult to wrap around ferrite grains, even partially, becomes prominent. Preferably, it is equal to or greater than 0.6% by weight. This is because, an amount of another element to be added to guarantee abrasion resistance can be reduced.
    Si: 0.5 to 2% by weight [0018] Si (silicon) is an element for reinforcing the tensile strength in each deposited metal, and a weld metal comprising the deposited metal and a molten base metal. In order to allow this function to be performed effectively, a Si content (Si quantity) is equal to or greater than 0.5% by mass. Preferably, it is equal to or greater than 0.7% by weight. At the same time, from the point of view of suppressing the occurrence of red scale (red rust), the amount of Si is equal to or less than 2% by mass. Preferably, it is less than or equal to 1.5% by weight. In the metal deposited according to the above modality, which is necessary to suppress the occurrence of red scale, for the following reason. Red scale consists mainly of Fe 2 O 3 , and occurs in a state where it is coated on a metal surface deposited in the form of fine powder and in a floury state. Red scale is extremely fragile. Although the red scale can be removed by pickling, a roughness of the surface on each deposited metal, and a weld metal comprising the deposited metal and a molten base metal, after pickling, becomes larger, so that the crack is most likely to occur.
    Mn: 0.5 to 2% by weight
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    9/40 [0019] Mn (manganese) is an element that is necessary to ensure the strength and hardness in each deposited metal, and a weld metal that comprises the deposited metal and a molten base metal. In order to allow this function to be exercised effectively, a content of Mn (Mn quantity) is equal to or greater than 0.5% by mass. Preferably, it is equal to or greater than 0.7% by weight. At the same time, from the point of view of suppression of the deficiency of hardness and weldability, the amount of Mn equal to or less than 2% by mass. Preferably, it is less than or equal to 1.5% by weight.
    Cr: 20 to 40% by weight [0020] Cr (Chromium) is an element that is essential to improve corrosion resistance in each deposited metal, and a weld metal that comprises the deposited metal and a molten base metal. In addition, Cr is an element for the formation of a carbide and, more specifically, an element that has the function of causing a carbide to be finely precipitated and hardened into ferrite grain crystals. Based on the precipitation of fine carbide hardening, abrasion resistance is enhanced. A Cr content (Cr amount) is equal to or greater than 20% by weight. Preferably, it is equal to or greater than 24% by weight. This is because, if the Cr amount is less than 20% by mass, desired corrosion resistance and abrasion resistance (hardness) cannot be obtained. At the same time, the amount of Cr is less than or equal to 40% by weight. Preferably, it is less than or equal to 36% by weight. This is because, if the amount of Cr is greater than 40% by mass, martensite is more
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    10/40 susceptible of being produced, which makes it more likely that the hardness is increased, and the toughness is deteriorated.
    Mo: 2 to 6% by weight [0021] Mo (Molybdenum) is an element to reinforce corrosion resistance in each deposited metal and a weld metal that comprises the deposited metal and a molten base metal. From the point of view of allowing this function to be performed effectively, a Mo content (amount of Mo) is equal to or greater than 2% by mass. Preferably, it is equal to or greater than 3.5% by weight. At the same time, from the point of view of a suppression situation where the infiltration of Faialite, that is, an oxide of Fe and Si (Fe2SiO4), is facilitated due to the segregation of limit grain steel from a molybdenum compound, the amount of Mo equal to or less than 6% by weight. Preferably, it is less than or equal to 4.5% by weight.
    Ni: 0.5 to 6% by weight [0022] Ni (Nickel) is an element to reinforce the corrosion resistance in each deposited metal, and a weld metal that comprises the deposited metal and a molten base metal. In order to allow this function to be exercised effectively, a Ni content (amount of Ni) is equal to or greater than 0.5% by mass. Preferably, it is equal to or greater than 0.7% by weight. At the same time, from the point of view of the situation in which a suppression situation where austenite is more likely to be produced, the amount of Ni is equal to or less than 6% by mass. Preferably, it is less than or equal to 1.5% by weight.
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    V: 1 to 5% by weight [0023] V (Vanadium) is an element that has the function of forming the precipitation hardening of a vanadium carbide (VC) in a deposited metal. V is added to improve the abrasion resistance in each deposited metal, and a weld metal comprising the deposited metal and a molten base metal. From the point of view of allowing this function to be performed effectively, a content of V (amount of V) is equal to or greater than 1% by mass. Preferably, it is equal to or greater than 1.5% by weight. At the same time, from the point of view of the suppression situation where the toughness is deteriorated due to the precipitation of a vanadium carbide in ferrite grain crystals, the amount of V is equal to or less than 5% by mass. Preferably, it is less than or equal to 2.5% by weight.
    W: 0.5 to 5% by weight [0024] W (Tungsten) is an element that has the function of forming the precipitation of hardening of a tungsten carbide (VC) in a deposited metal. W is added to improve the abrasion resistance in each deposited metal and a weld metal that comprises the deposited metal and a molten base metal. In order to allow this function to be performed effectively, a W content is equal to or greater than 0.5% by mass. Preferably, it is equal to or greater than 0.7% by weight. At the same time, from the point of view of a suppression situation where the toughness is the deterioration due to the precipitation of a tungsten carbide in ferrite grain crystals, the W value is equal to or less than 5% in
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    12/40 dough. Preferably, it is less than or equal to 1.5% by weight.
    [0025] The metal deposited according to the above modality satisfies the composition of components above, and the rest of the composition is Fe and unavoidable impurities. The unavoidable impurities include components, such as Al (Aluminum) and Ca (Calcium), to be inevitably mixed with a welding material for use in the welding accumulation, during a welding material production process [0026] Like others elements, the metal deposited according to the above modality may also contain (A) P: 0.03% by mass or less (except for 0% by mass) and / or S: 0.02% by mass or less (with the exception of 0% by weight), and / or (B) in total 15% by weight or less (except 0% by weight) of one or more selected from the group consisting of Ti, Co, Cu, Zr, Nb, Pd, Ag, Sn, Hf, Ta, Pt, Au and Pb. The reasons for defining these ranges are as follows.
    P: 0.03% by weight or less [0027] P (Phosphorus) is an element that is segregable as an impurity in the boundary grains in steel. When the steel material is stretched in the direction of the design by forging, rolling, etc., a segregated zone of P is formed. Ferrite (a-Fe) is formed in the segregated zone, and C is excluded from the segregated zone. As a result, Fe is formed zonally in the segregated zone of P, and perlite is formed zonally in the remaining region. Such a segregated zone of P is generally called a ferrite band and when the ferrite band is formed, ductility in the direction
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    13/40 perpendicular to the zone is deteriorated. In the case where a steel material subjected to forging or rolling is used as a base metal and a deposited metal is formed on a surface of the base metal by welding accumulation using a welding material, a P content (amount of P) is equal to or less than 0.03% by mass. This is because, if P in the deposited metal is greater than 0.03% by mass, a problem of deterioration in the ductility of the band due to ferrite. In other cases, the amount of P may be greater than 0.03% by weight.
    S: 0.02% by mass or less [0028] S (Sulfur) is an element for the formation, in steel, of MnS as an inclusion of base sulfide, which is secreted during the hot work of the steel material, causing the brittleness of the steel material. In the case where a steel material subjected to forging or rolling is used as a base metal and a deposited metal is formed on a surface of the base metal by accumulation of welding using a welding material, an S content (amount of S) is equal to or less than 0.02% by mass. This is because, if S in the deposited metal is greater than 0.02% by mass, the steel material is weakened, causing a problem that is more likely to be cracked. In other cases, the S value may be greater than 0.02% by weight.
    [0029] Total of 15% by weight or less, from one or more selected from the group consisting of Ti, Co, Cu, Zr, Nb, Pd, Ag, Sn, Hf, Ta, Pt, Au and Pb [0030] A component capable of expressing a different effect than the effects of the present invention, without harming the deposited metal according to the modality
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    14/40 above includes Ti (titanium), Co (Cobalt), Cu (Copper), Zr (Zirconium), Nb (Niobium), Pd (Palladium), Ag (Silver), Sn (Tin), Hf (Hafnium), Ta (Tantalum), Pt (Platinum), Au (Gold) and Pb (Lead). To express the other effects in addition to the effects of the present invention, the metal deposited according to the above embodiment can contain one or more of the above elements in a total amount of 15% by weight or less. This is because, since the content of the elements mentioned above does not exceed 15% by mass in total, the metal deposited according to the previous modality is maintained in a microstructure where a matrix is composed of a plurality of ferrite grains and a plurality of cementite grains are precipitated from boundary ferrite grains, more specifically, in a polycrystalline microstructure, where a ferrite phase as a matrix exhibits crystalline characteristics and at least part of the periphery of the ferrite crystal is covered by a cementite, so that it becomes possible to prevent deterioration of corrosion resistance, abrasion resistance and toughness.
    [0031] Preferably, the metal deposited according to the above embodiment has a metal microstructure where the matrix comprises a plurality of ferrite grains, and a plurality of cementite grains are precipitated from ferrite bound grains. More preferably, the metal deposited according to the above embodiment has a ferrite microstructure as a matrix, wherein the ferrite microstructure has a structure where cementite wraps around the peripheries of ferrite grains. The reason is as follows.
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    15/40 [0032] The ferrite microstructure is able to stably absorb and store hydrogen, as compared to an austenite microstructure and a martensite microstructure, so that there is an advantageous effect that is less likely to undergo hydrogenation and cracks, even in an acidic environment. That is, in the ferrite microstructure, even though hydrogen is generated due to corrosion and incorporated into a steel material, as hydrogen will not be accumulated at the ferrite site, so that the excellent resistance to hydrogen fragility is exhibited in an acidic atmosphere. , as compared to an austenite microstructure and a martensite microstructure. In addition, the plurality of cementite grains precipitated in the ferrite bound grains maintain the connection between the respective ferrite grains, more preferably, the cementite surrounds the ferrite, so that the ferrite microstructure is less likely to be cracked, as compared to an austenite microstructure and a martensite microstructure.
    [0033] In this regard, a metal microstructure of the deposited metal disclosed in Patent Document 1 is an acicular carbide microstructure. In the acicular carbide microstructure, hydrogen is susceptible to being accumulated at an interface between acicular carbide and ferrite, so that hydrogen inducing cracking is more likely to occur. In particular, it is more likely to be split in one direction. Compared with the acicular carbide microstructure, the ferrite microstructure above is low in residual stress and microstructurally stable, so there is an advantage
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    16/40 that is less likely to be cracked.
    [0034] As illustrated in the following Example, almost no difference in composition occurs between the welding build-up material and the deposited metal according to the above modalities, except that only the respective contents of Cr, Mo and Ni are slightly reduced. Thus, like the welding material according to the above modality, a material having the same composition as that of the deposited metal according to the above modality, or a material having a composition in which the respective contents of Cr, Mo and Ni slightly larger than those of a target composition can be prepared.
    [Element with Deposited Metal] [0035] An element of a deposited metal, according to an embodiment of the third aspect of the present invention, comprises a steel material that serves as a base metal, and a welding accumulation of the metal deposited on a surface of the steel material. This metal is deposited on the deposited metal according to the above modality.
    [0036] In the element according to this modality, the base metal and the deposited metal are joined through a zone affected by heat and a molten base metal.
    [0037] The base metal is not particularly limited, as long as it is a steel material. In the case where the base metal is used as a material for forming a container for a sprayer, reactor or the like, which includes, for example, several stainless steels, S25C steel, SC49 steel and SS400 steel, as mentioned above. Among these steel materials, in view of the dilution of suppression of
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    17/40 base metal, it is preferable to use, as the base metal, a steel material having the same composition as that of the deposited metal according to the above modality. However, the base metal essentially requires strength and toughness, while the deposited metal mainly requires hardness and abrasion resistance. Thus, it is currently difficult to employ, like the base metal, a steel material having the same component composition as that of the deposited metal. For this reason, it is desirable to sequentially build up the weld on a material (deposited metal) as much as possible, while positioning the base metal in a vertical posture. This makes it possible to suppress, to some extent, the interdiffusion of the element component (mainly, Fe) between the molten base metal and the deposited metal, due to the force of gravity and convection.
    [0038] The element according to this modality can be conveniently used as a processing vessel installed in a processing apparatus, such as a sprayer or a reactor, for the treatment of a target substance comprising an acid, such as hydrochloric acid or sulfuric acid, under a corrosive acid environment having pH = about 7.0 to about 4.2 and in a temperature range from room temperature to about 200 ° C. The metal deposited according to the above modality can be formed in a internal wall of the processing container by welding accumulation, which makes it possible to improve the corrosion resistance and abrasion resistance of the processing container and, therefore, to increase its useful life.
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    [0039] Although the present invention is described more specifically below on the basis of the example, it should be understood that the following example is not intended to restrict the technical scope of the present invention, but can be implemented with appropriate modifications and modifications made to an extent capable of complying with the above and below content. Accordingly, such changes and modifications should be understood to be within the technical scope of the present invention.
    EXAMPLE [0040] The following description will be made of inventive and comparative examples to demonstrate the effects of the present invention.
    [0041] Table 1 below illustrates the respective welding compositions of different materials. Note that the balance in each of the welding materials comprises unavoidable impurities in addition to Fe or Co described in Table 1.
    [Table 1]
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    19/40
    OOsm Faith Faith Faith Faith Faith Faith Faith Faith Faith Faith Faith Faith Faith Faith Faith Faith Faith Co Co Faith Faith 1.0 1.0 1.0 1.0 2.0 1.0 1.0 1.0 1.0 1.0 1.0 1.0 1.0 1.0 1.0 1.0 Ot — 1 0 c-1 5.0 1 1 > 2.0 2.0 2.0 2.0 O^ P 2.0 2.0 2.0 2.0 2.0 2.0 2.0 2.0 2.0 2.0 2.0 2.0 l 1 1 1 COMPOSITION (MASS%) Hs 1.0 1.0 1.0 1.0 2.0 1.0 1.0 1.0 1.0 1.0 1.0 1.0 1.0 1.0 1.0 1.0 1.0 1 1 1 02 O^ P O^ P O^ P O^ P O^ P O^ P O^ P O^ P O^ P O^ P O^ P O^ P O^ P O^ P O^ P D C-1 1.0 1 1 0.3 kOt — 1 Cr 35.0 35.0 35.0 35.0 35.0 35.0 35.0 35.0 35.0 35.0 35.0 35.0 35.0 50.0 19.0 35.0 35.0 33.0 26.0 13.0 31.0 ω <0.02 <0.02 <0.02 <0.02 <0.02 <0.02 <0.02 <0.02 <0.02 <0.02 <0.02 <0.02 <0.02 <0.02 <0.02 <0.02 <0.02 <0.02 <0.02 <0.02 <0.02<0.03 <0.03 <0.03 <0.03 <0.03 <0.03 <0.03 <0.03 <0.03 <0.03 <0.03 <0.03 <0.03 <0.03 <0.03 <0.03 <0.03 <0.03 <0.03 <0.03 <0.03 Mn 1.0 1.0 1.0 1.0 1.0 1.0 1.0 1.0 1.0 1.0 1.0 3.0 0.2 1.0 1.0 1.0 1.0 1 1 kOO 1.6 Si 1.2 1.2 1.2 2.0 1.2 1.2 1.2 1.2 3.0 2.5 0.3 1.2 1.2 1.2 1.2 1.2 1.2 1 1 0.2 0.7 u kOO 0.4 0.25 kOO kOO 1.2 1.5 1.8 kOO kOO kOO kOO kOO kOO kOO kOO kOO 2.5 1.0 0.4 4.5 t — 1 (M ro ^ P LO kO 1> 00 ΟΊ 10 11 12 13 14 15 16 17 18 19 20 21 EXAMPLE EXAMPLE 0COMPARATIVE
    [0042] Table 2 below illustrates the standard chemical component of carbon steel for the use of the structural machine (S25C steel), used as a base metal, that is, a welding target. Note that the balance of S25C steel comprises unavoidable impurities, in addition to Fe described in Table 2.
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    20/40 [Table 2]
    MATERIAL COMPOSITION (MASS%) Ç Si Mn P s SWING S25C 0.20-0.30 0.15 ~ 0.40 0.30-0.60 <0.045 <0.045 Faith
    [0043] Welding conditions are as follows. Each of the welding materials illustrated in Table 1 was used for the welding accumulation the welding material on a base metal surface consisting of S25C steel, in order to form a weld accumulation layer (weld metal accumulation). ), with an average thickness of about 3 mm. Before welding, the base metal was heated from room temperature to 300 ° C, at a rate of temperature increase of 100 ° C / h. Then, the welding build-up was carried out under the condition that the base metal is carried out isothermally at 300 ° C. After welding was completed, the base metal was cooled to room temperature at a cooling rate of 20 ° C / h. The welding build-up was carried out in a flat position at a welding current of 280 A and a welding voltage of 30 V, and a heat input during welding was 2.0 kJ / mm.
    [0044] Table 3 below illustrates a composition of a surface layer (deposited metal), in each of the metals the accumulation of weld obtained by welding. Note that the balance in each of the surface layers comprises unavoidable impurities, in addition to Fe or Co described in Table 3. The surface layer, a region that has a depth of 1 mm or less from
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    21/40 of the surface. The weld accumulation metal region with a depth of 1 mm was mechanically scraped from the surface layer. Then, the scraped portion was dissolved in a given acid and analyzed quantitatively by chemical analysis, and an analysis result was determined as a component of a deposited metal composition. In the chemical analysis, C (carbon) and Si were analyzed quantitatively, respectively, using an infrared absorption method, and the remaining elements were analyzed quantitatively by ICP atomic emission spectrophotometry. Table 3 below is a result of a quantitative analysis of the deposited metals determined in this way.
    [Table 3]
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    22/40
    o °ωω SWING Faith Faith Faith Faith Faith Faith Faith Faith Faith Faith Faith Faith Faith Faith Faith Faith Faith Co Co Faith Faith COMPOSITION co (M00 t — 1 l>ΟΊ (MO coO (MO OO LOΟΊ ΟΊΟΊ t — 1 O O OO 00ΟΊ l>ΟΊ coO ΟΊ00 21 coLO 1 1 O O O O (M t — 1 t — 1 t — 1 O O t — 1 t — 1 t — 1 O O t — 1 O O ^ P > kO t — 1 ΟΊ 00 ΟΊ00 O[> (M00 kO00 0000 [>[> l>00 l>ΟΊ t — 1 ΟΊ 00[> kO[> [>[> t — 1 ΟΊ 00 1 1 1 1 t — 1 t — 1 t — 1 t — 1 CO t — 1 t — 1 t — 1 t — 1 t — 1 t — 1 t — 1 t — 1 t — 1 t — 1 t — 1 t — 1 H ΟΊ00 kO00 00[> 00 O[> 0000 (M00 ΟΊl> t — 1 00 l>00 ΟΊ00 t — 1 ΟΊ l>00 kO00 ΟΊ00 00 ΟΊ 1 1 1 O O O O t — 1 O O O O O O O O O O O O 02 3.23 3.22 3.00 3.16 3.30 3.27 3.16 3.18 3.24 3.26 3.06 3.21 3.07 3.12 3.05 8.32 l>00O 1 1 0.27 0.70 Cr l> t — 1 O kOO ΟΊ OO l> 00 (M ι — 1 [>[> l> (MO O t — 1 O coCN O co kO co00 ΟΊΟΊ coι — 1 coO 28. 28. 28. 27. 28. 27. 27. 28. kO(M 25. 28. 28. 28. 41. kO ι — 1 27. 27. 21. 29. (M ι — 1 27. ω (MO (MO (MO (MO (MO (MO (MO (MO (MO (MO (MO (MO (MO (MO (MO (MO (MO (MO (MO (MO (MO OV OV OV OV OV OV OV OV OV OV OV OV OV OV OV OV OV OV OV OV OV coO coO COO COO COO COO COO COO COO COO COO COO COO COO COO COO COO COO COO COO COO OV OV OV OV OV OV OV OV OV OV OV OV OV OV OV OV OV OV OV OV OV Mn 1.03 1.04 0.98 1.95 O00O 0.95 1.01 1.03 1.01 1.02 1.02 2.90 00(MO 1.03 1.01 1.03 1.02 l 1 0.59 1.5 Si 1.15 1.18 1.17 1.95 0.99 1.13 1.08 1.04 2.89 2.41 0.27 1.13 1.2 1.18 1.12 1.11 1.09 1 1 0.22 0.97 u 58 (MCO coCN t — 1 <0 co<0 LO ι — 1 31 kOLO .58 O<0 CO<0 59 58 .58 t — 1 <0 O<0 co<0 00ι — 1 kO ι — 1 l>CO <0 O O O O O t — 1 t — 1 t — 1 O O O O O O O O O (M t — 1 O co t — 1 (M co ^ P LO kO l> 00 ΟΊ The ι — 1 t — 1 ι — 1 (M ι — 1 COι — 1 ι — 1 LO ι — 1 kO ι — 1 l> ι — 1 00ι — 1 ΟΊ t — 1 20 21 EXAMPLE EXAMPLE 0 COMPARATIVE
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    23/40 [0045] All welding materials from Examples 1-7 and Comparative Examples 8-17, 20 and 21 are Fe alloys. It is observed that, in the deposited metal, a concentration (content) of each Cr , Mo and Ni tends to decrease slightly, compared to the welding material (raw material). This is considered to be because Fe as a main constituent element of the base metal is dispersed in the weld accumulation metal during welding, to dilute the concentration of each of Cr, Mo and Ni. An amount of the decrease in the concentration of each of Cr, Mo and Ni is about 20%. On the other hand, as with each of the other elements (C, Si, Mn, P, S, V and W), with the exception of Cr, Mo and Ni, the deposited metal is kept at approximately the same concentration as in material welding ( feedstock).
    [0046] Although both welding materials in Comparative Examples 18 and 19 are Co alloys, Fe was detected as an alloying element. More specifically, Fe is not originally contained in each of the welding materials of Comparative Examples 18 and 19. However, due to the dispersion of Fe from the base metal, Fe was mixed in them, respectively, at 9.57% and 7.98%, although not described in Table 3. As a result, in particular in Comparative Example 18, despite a decrease in the concentration of each of Cr and W is observed, an amount of the decrease in the concentration of each of Cr and W is about 30%, which is not that big. In addition, as with each of some elements (C, P, S), with the exception of Cr and W, the deposited metal is kept at approximately the same concentration as that of the
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    24/40 welding (raw material). In Comparative Example 19, no major change in the concentration of each of the elements contained is observed, so that the difference between the respective compositions of the welding material and the deposited metal is small. Both welding materials of Comparative Examples 20 and 21 are Fe alloys. In this case, a decrease in the concentration of each of Cr and Mo is observed. However, the level of reduction is small. In addition, as with each of some elements (C, Si, Mn, P and S), with the exception of Cr Mo, the deposited metal is kept at approximately the same concentration as that of the welding material (raw material). From the results presented above, it can be said that the difference between the respective compositions of the welding material and the deposited metal is small.
    [0047] A result obtained by subjecting each of the deposited metals illustrated in Table 3 to measure the surface hardness will be described below. As the surface hardness, Rockwell hardness and Vickers hardness were measured. More specifically, based on the Rockwell test specified in JIS G 0202, a circular cone (tip: 0.3 mm) having an apex angle of 120 degrees was pressed from the side of a weld accumulation on a metal surface (surface of the deposited metal) with a load of 60 kgf, and a permanent tooth depth from a reference surface was read after the load is returned to a reference load of 10 kgf. Then, Rockwell hardness was calculated using a Rockwell hardness calculation formula. In calculating Rockwell hardness, the C scale was used. THE
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    25/40 Vickers hardness was measured using a Vickers hardness tester MVK-E produced by Akashi Corp. More specifically, a pyramid-shaped penetrator composed of a quadrilateral diamond in which an angle between the opposite faces is 136 degrees has been pressed against the weld buildup on the metal surface (deposited metal surface), and a surface area S (mm2) of a tooth remaining after removing a load was calculated from a length d (mm) of a diagonal line of the tooth. Then, the Vickers hardness was calculated based on the relationship between the test load and the surface area, using a given calculation formula.
    [0048] FIG. 1 illustrates a respective Rockwell hardness of the deposited metals. Comparative Examples 18 and 21 having a high concentration of W or C exhibit a high hardness. In contrast, a hardness for each of the metals deposited in Examples 1 to 7 is equal to or greater than 30 in terms of Rockwell hardness, which meets an acceptance criterion value (Rockwell hardness of 30 or more), although it is low when compared to Comparative Examples 18 and 21. Thus, they are at a satisfactory level as a deposited metal.
    [0049] FIG. 2 illustrates Vickers hardness of the respective deposited metals. Comparative Examples 18 and 21 having a high concentration of W or C exhibit a high hardness. In contrast, a hardness of each of the metals deposited in Examples 1 to 7 is equal to or greater than 300, in terms of Vickers hardness, which meets an acceptance criterion value (Vickers hardness of 300 to
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    500), although it is low when compared to Comparative Examples 18 and 21. Thus, they are at a satisfactory level as a deposited metal. In this respect, an upper limit value is defined as the Vickers hardness acceptance criterion value, because Vickers hardness and toughness have an exchange ratio. It can be said that Examples 1 to 5 are high in strength compared to Comparative Examples 18 and 21.
    [0050] A result obtained by subjecting each of the weld accumulation metals (deposited metals) illustrated in Table 3 for a test to assess abrasion resistance will be described below. The abrasion resistance was assessed by the soil abrasion test specified in the ASTM G 65 standard. FIG. 3 is a conceptual diagram illustrating a soil abrasion tester. As illustrated in FIG. 3, a roller coated with rotating rubber 2 is fixed in sliding contact with the test piece 1 and silica sand 6 is supplied from a hopper 5 to a position between the test piece 1 and the roller covered with rotating rubber 2 The pressure force of the specimen 1 against the rotating rubber-covered cylinder 2 is given by a lever arm 3 having a weight of 4 hanging from its free end. The abrasion resistance of each of the deposited metals was evaluated by pressing a surface layer (deposited metal) of test specimen 1 which consists of a weld metal build-up, against the rotating rubber-covered cylinder 2, with a load of 13.3 kgf and the rotating drum 2 for a predetermined number of revolutions (6000 revolutions) to measure the weight loss by
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    27/40 abrasion of piece 1 after 2000 rotations, after 4000 rotations, and after the study is completed (after 6000 rotations).
    [0051] FIGS. 4 to 6 illustrate the results of the evaluation of the abrasion resistance of the deposited metals, in which the horizontal axis represents the number of rotations of the sliding of the drum 2, and the vertical axis represents a weight loss by abrasion. As illustrated in FIG. 4, among the deposited metals, Comparative Example 21 showed the highest resistance to abrasion. Specifically, a weight loss by abrasion of piece 1 after drum 2 rotation to 6000 revolutions was 1 g or less. On the other hand, as illustrated in FIGS. 4 to 6, an abrasion weight loss in each of Examples 1 to 5 exhibited the second highest abrasion resistance just behind Comparative Example 21. Specifically, a weight loss after rotating abrasion of drum 2 for 6000 revolutions was 4 g or less. Compared to them, as illustrated in FIG. 4, Comparative Examples 18 to 20 have been evaluated which are lower in abrasion resistance. Specifically, the weight loss of the specimen after rotation of drum 2 to 6000 revolutions was 5 g or more.
    [0052] FIG. 5 is a graph for comparing the respective abrasion weight losses in Examples 1 to 3, 6 and 7 and in Comparative Example 8, in which only the concentration of C (C content) is changed. As illustrated in FIG. 5, a result was obtained that the abrasion resistance becomes more deteriorated (the weight loss is increased by abrasion), as the C concentration becomes higher. This is considered to be because the resistance becomes more
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    28/40 deteriorated as the concentration C becomes higher, which accelerates the fragility, causing an increase in aggressive abrasion.
    [0053] FIG. 6 is a graph, comparing abrasion weight loss of Examples 1 and 4 and Comparative Examples 9 to 11 in which only the Si concentration (Si content) is changed. As illustrated in FIG. 6, a result was obtained that the abrasion resistance becomes more deteriorated (the weight loss is increased by abrasion), as the Si concentration becomes higher. This is considered to be because the resistance becomes more deteriorated as the Si concentration becomes greater, which accelerates the brittleness, causing an increase in aggressive abrasion, as in the case of the C. concentration. and 21 have less abrasion weight loss than Examples 1 to 7, Comparative Example 11 is not suitable for practical use, due to too low a Si content and Comparative Example 12 is not suitable for practical use, due to an excessive high C content.
    [0054] Then, each of the weld accumulation metals (deposited metals) illustrated in Table 3, was subjected to the following corrosion test to assess its corrosion resistance. A corrosion test procedure is as follows. First, a test piece (coupon) that is 15 x 15 x 1.5 mm in size was taken from the surface layer side of each of the weld accumulation metals, and used as a sample. Then an aqueous solution (mixed acid, aqueous solution), obtained by mixing hydrochloric acid (HCl) and acid
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    29/40 sulfuric (H2SO4) together in order to define a ratio of molar concentration of HCl to H2SO4 2: 1 was diluted with water exchanging ions while adjusting the pH to 2.0, to prepare a test solution, and each sample was immersed in the test solution maintained at 80 ° C for 24 hours. Subsequently, the weight loss after the corrosion test was measured. Corrosion resistance was assessed based on a level of corrosion weight loss.
    [0055] FIGS. 7 and 8 illustrate a result of the corrosion test of the deposited metals (it is noted that the scale of the horizontal axis is different between FIGS. 7 and 8). The corrosion test was performed under the condition that n = 3 and an average corrosion rate was obtained from the mass loss corrosion of the three samples. As illustrated in FIG. 7, each of Comparative Examples 20 and 21 has an extremely large average corrosion rate, and in Comparative Example 18 it has a relatively large average corrosion rate, which shows that they are inferior to other samples (Examples 1 and 5 and Example Comparative 19), in terms of corrosion resistance. In addition, as illustrated in FIG. 8, in Examples 1 to 7 and Comparative Examples 8 to 17, samples from Comparative Examples 9 and 10 each with a high Si concentration (Si content), the sample from Comparative Example 12, which has a high Mn concentration (Mn content), and the sample from Comparative Example 17 which has a low Mo content (Mo content), has a relatively high average corrosion rate. Compared to then, each of the samples in Examples 1 to 7 has an average corrosion rate of 0.01 mm / year or less, which satisfies an acceptance criterion value (rate of
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    30/40 average corrosion of 0.01 mm / year or less). That is, they have excellent resistance to corrosion.
    [0056] The above results are collectively illustrated in Table 4 below. Table 4 below illustrates Rockwell hardness, Vickers hardness and average corrosion rates of examples of the invention and comparatives. In Table 4, a sample having a Rockwell HRc hardness of 30 or more (acceptance) is indicated as good, and a sample having a Rockwell HRc hardness of less than 30 (nonacceptance) is indicated as poor. In addition, a sample having a Vickers hardness of 300 to 500 (acceptance) is indicated as good, and a sample that has a Vickers hardness outside the range (non-acceptance) is indicated as poor. As shown in Table 4, Examples 1 to 7 are appropriate in terms of Rockwell hardness and Vickers hardness (both were rated as good) and low average corrosion rate. Compared to then, comparative examples 8 to 10, 12, 17, 18, 20 and 21 are excessively high in average corrosion rate and lower in corrosion resistance. In addition, Comparative Examples 15 and 17 are excessively low at Vickers hardness and Comparative Examples 14 and 21 are excessively high at Vickers hardness.
    TABLE 4
    ToughnessROCKWELL(HRc) VICKERS Hardness (Hv) Average corrosion rate (mm / year) 1 GOOD GOOD 0.005 2 GOOD GOOD 0.006 3 GOOD GOOD 0.005
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    EXAMPLES 4 GOOD GOOD 0.010 5 GOOD GOOD 0.009 6 GOOD GOOD 0.009 7 GOOD GOOD 0.010 EXAMPLECOMPARATIV 8 GOOD GOOD 0.011 9 GOOD GOOD 0.035 10 GOOD GOOD 0.029 11 GOOD GOOD 0.005 12 GOOD GOOD 0.026 13 GOOD GOOD 0.009 14 GOOD POOR 0.009 15 GOOD POOR 0.006 16 GOOD GOOD 0.004 17 GOOD POOR 0.015 18 GOOD GOOD 0.2 19 GOOD GOOD 0.010 20 GOOD GOOD 1.9 21 GOOD POOR 3.9
    [0057] A result of microscopic observation of a microstructure in cross section of each of the weld metal accumulations (deposited metals) illustrated in Table 3 will be described below. The weld metal accumulation layer was formed on a base metal made of S25C steel having an average thickness of about 3 mm and a test piece was cut by machining so that the base metal is partially joined to the accumulation layer weld metal. Then, the test piece was buried in the resin and the resin block obtained was polished to
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    32/40 prepare a sample that has an exposed cross section of the weld metal accumulation layer. After submitting to the sample the engraving using aqua regia, a central portion of the known thickness of the thicknesswise (deposited metal) was observed by an optical microscope with a magnification of 400 times. FIGS. 9-11 are optical micrographs, indicating the respective transverse microstructures of the deposited metals.
    [0058] Example 1 has a polycrystalline microstructure in which the crystal grain size is in the range of 20 to 40 µm and a matrix of a ferrite phase. Carbide (Fe3C: cementite) is observed in grained crystal boundaries of the polycrystalline microstructure and it can be determined that the carbide exists in such a way that it wraps around the ferrite crystal grains. In Examples 6 and 7 and Comparative Example 8, in which the concentration of C is increased in relation to that of Example 1, a change in the polycrystalline microstructure is observed together with the increase in the concentration of C. Specifically, the thickness of a layer of carbide (Fe3C: cementite) to be precipitated in the crystal limit grains becomes larger with the increase in the concentration of C. However, in Example 7, a polycrystalline microstructure similar to that of Example 1 is maintained. On the other hand, in Comparative Example 8, the polycrystalline microstructure observed in Example 1 is completely interrupted, so that a non-polycrystalline microstructure is formed in which carbide (cementite) wraps around the peripheries of the ferrite crystal grains. It can be said that the chemical composition of the metal deposited in Example 7 is close to a critical condition
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    33/40 for the formation of the polycrystalline microstructure in the cementite wraps around the peripheries of the ferrite crystal grains.
    [0059] Each of Examples 2 and 3 has a polycrystalline microstructure similar to that of Example 1. Although carbide (Fe3C: cementite) is observed in grains
    limits of grains crystal of ferrite like a matrix, the carbide not exists in such a way which involves completely grains in crystals of ferrite (a plurality in grains in cementite are locally
    precipitated on boundary ferrite grains, so that cementite partially involves ferrite crystal grains). This trend is more significantly exposed in Example 3, compared to Example 2. It can be said that the chemical composition of the deposited metal of Example 3 is close to a critical condition for the formation of the polycrystalline microstructure in which cementite partially surrounds the grains of ferrite crystals.
    [0060] Example 4 has a polycrystalline microstructure similar to that of Example 1. In Example 4 and Comparative Examples 9 and 10, in which the Si concentration is increased in relation to that of Example 1, a change in the polycrystalline microstructure is observed together with the increase in Si concentration. Specifically, the thickness of a carbide layer (Fe3C: cementite) to be precipitated in the crystal bound grains becomes greater with the increase in Si concentration, as in Comparative Examples 9 and 10. In this case, a Si oxide (SiO2) or a Si oxide compound (Fe2SiO4) is likely to be simultaneously precipitated in the boundary grains of the crust.
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    Comparative example 9, in which the Si concentration is increased from that of Example 1 above to 3.0%, has a polycrystalline microstructure similar to that of Example 1. However, due to the occurrence of aggregation of a precipitated substance in the limit grains of crystal, an ability to wrap around ferrite crystal grains is impaired, so a precipitated substance will also be seen in the crystal grains.
    [0061] In Comparative Example 11, in which the Si concentration is reduced in relation to that of Example 1, the polycrystalline microstructure observed in Example 1 is completely interrupted, so that the polycrystalline microstructure does not form in which carbide (cementite) surrounds around the peripheries of ferrite crystal grains. It is understood that the chemical composition of the deposited metal of Comparative Example 11 fails to form the polycrystalline microstructure in which cementite surrounds the peripheries of the ferrite crystal grains.
    [0062] Comparative example 15 has a fine complicated polycrystalline microstructure. That is, it makes up approximately the entire region of a metal microstructure that is formed as a martensite phase.
    [0063] Example 5 has a polycrystalline microstructure similar (analogous) to this in Example 1. The matrix of Example 5 is a ferrite phase. Carbide (Fe3C: cementite) is observed in crystal bound grains of the polycrystalline microstructure and it can be determined that the carbide exists in such a way that it wraps around ferrite crystal grains. Comparative Examples 18 and 19 each have a polycrystalline microstructure with a
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    35/40 dendrite configuration. Approximately the entire region of the metal microstructure is formed as an austenite phase. In Comparative Example 20, approximately, the entire region of a metal microstructure is formed as a martensite phase. A white looking portion in the metal microstructure of Comparative Example 20 is carbide (Fe3C: cementite). Comparative example 21 has a complicated polycrystalline microstructure in which three phases: a ferrite phase, a martensite phase and a carbide phase, are mixed. As above, we
    Comparative Examples Polycrystalline is not the 21, the microstructure formed in which carbide (cementite) wraps around the peripheries of ferrite crystal grains. In Comparative Example 14, a Cr content of the welding material is 50% by mass, that is, it is greater than 40% by mass, so that martensite is more susceptible to being produced and that is why it is difficult to form a matrix as a ferrite phase.
    [0064] Tenacity and strength in each of the deposited metals of Examples 1 to 7 and Comparative Example 13 were verified. As a result, Examples 1 to 7 exhibited satisfactory values. On the other hand, Comparative Example 13 with a low Mn content was inferior to that of Examples 1 to 7, in terms of toughness and strength and could not present satisfactory values.
    [0065] As described above in detail, according to one aspect of the present invention, a welding buildup material is provided which contains C: 0.2 to 1.5% by weight, Si: 0.5 to 2% by mass, Mn: 0.5 to 2% by mass, Cr: 20 to 40% by mass, Mo: 2 to 6% by mass, Ni: 0.5 to 6% by mass,
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    V: 1 to 5% by mass and W: 0.5 to 5% by mass, with the remainder being Fe and unavoidable impurities.
    [0066] Preferably, in the welding build-up material of the present invention, a deposited metal contains: C in an amount of 0.6 to 0.8% by weight; Si in an amount of 0.7 to 1.5% by mass; Mn in an amount of 0.7 to 1.5% by mass; Cr in an amount of 24 to 36% by weight; Mo in an amount of 3.5 to 4.5% by weight; Ni in an amount of 0.7 to 1.5% by weight; V in an amount of 1.5 to 2.5% by mass and W in an amount of 0.7 to 1.5% by mass.
    [0067] The welding build-up material of the present invention may also contain P: 0.03% by weight or less, and S: 0.02% by weight or less.
    [0068] The welding build-up material of the present invention may further contain one or more selected from the group consisting of Ti, Co, Cu, Zr, Nb, Pd, Ag, Sn, Hf, Ta, Pt, Au and Pb in a total amount of 15% by mass or less.
    [0069] According to another aspect of the present invention, a deposited metal is provided, which is produced by the welding accumulation, where the deposited metal contains C: 0.2 to 1.5% by mass, Si: 0, 5 to 2% by weight, Mn: 0.5 to 2% by weight, Cr: 20 to 40% by weight, Mo: 2 to 6% by weight, Ni: 0.5 to 6% by weight, V: 1 to 5% by mass and W: 0.5 to 5% by mass, with the remainder being Fe and unavoidable impurities.
    [0070] According to the above characteristic, the deposited metal of the present invention produced by the welding accumulation is formed a metal microstructure that has a ferrite matrix, in which cementite surrounds
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    37/40 at least a part of the periphery of the ferrite grains. The ferrite matrix contains Cr, Mo and Ni. Ferrite is resistant to the hydrogenation faragility compared to austenite and martensite, and corrosion resistance is increased based on Cr, Mo and Ni. Thus, the deposited metal of the present invention has an advantageous effect of being able to suppress hydrogenation and cracking brittleness, and keep residual stress low and stable, even in an acidic environment, and has excellent corrosion resistance and abrasion resistance. In addition, it has mechanical properties that have a good balance between hardness and toughness.
    [0071] An amount of Si in the deposited metal of the present invention is in the range of 0.5 to 2% by mass, which is less than in the deposited metal disclosed in Patent Document 1. Thus, a crack due to the red scale it is less likely to occur.
    [0072] Preferably, the deposited metal of the present invention contains: C in an amount of 0.6 to 0.8% by weight; Si in an amount of 0.7 to 1.5% by mass; Mn in an amount of 0.7 to 1.5% by mass; Cr in an amount of 24 to 36% by weight; Mo in an amount of 3.5 to 4.5% by weight; Ni in an amount of 0.7 to 1.5% by weight; V in an amount of 1.5 to 2.5% by mass and W in an amount of 0.7 to 1.5% by mass.
    [0073] According to this configuration, corrosion resistance, abrasion resistance and hardness can be further improved.
    [0074] The deposited metal of the present invention may still contain P: 0.03% by weight or less and S: 0.02% by weight
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    38/40 mass or less.
    [0075] The deposited metal of the present invention may also contain one or more selected from the group consisting of Ti, Co, Cu, Zr, Nb, Pd, Ag, Sn, Hf, Ta, Pt, Au and Pb, in a total amount 15% by mass or less.
    [0076] Preferably, the deposited metal of the present invention has a microstructure where a metal matrix comprises a plurality of ferrite grains and a plurality of cementite grains are precipitated from ferrite bound grains. More preferably, the metal microstructure of the deposited metal is a polycrystalline microstructure with a matrix formed as a ferrite phase, in which there is in the grain boundary cementite of ferrite crystal grains, while wrapping around the peripheries of the grains of ferrite crystal.
    [0077] According to this characteristic, a plurality of cementite grains precipitated on the ferrite limit grains maintain the respective connections between the ferrite grains, with more preference, the cementite surrounds the ferrite, so that the ferrite microstructure as matrix it is less likely to be cracked compared to an austenite microstructure and a martensite microstructure and the resistance to acid corrosion is higher.
    [0078] In accordance with yet another aspect of the present invention, there is provided an element comprising a steel material which serves as a base metal and an accumulation of welded deposited metal on a surface of the steel material, on which the deposited metal
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    contains C: 0.2 to 1.5% in mass, Si : 0.5 to 2% in mass, Mn: 0.5 to 2% by weight, Cr: 20 to 40% in bulk, Mo: 2 to 6% in mass, Ni: 0.5 to 6% by mass, V: 1 at 5% by mass and W: 0.5 to 5% by mass, as remaining being Fe and impurities inevitable. [0079] From wake up with this configuration, accumulation of
    welded deposited metal on the surface of the steel material, such as a base metal exhibits excellent corrosion resistance and abrasion resistance and exhibits mechanical properties having a good balance between hardness and toughness, so that the element can be properly used as an element sprayer, reactor or any other mechanical device for the treatment of an acidic substance.
    [0080] Preferably, in the element of the present invention, the deposited metal contains: C in an amount of 0.6 to 0.8% by weight; Si in an amount of 0.7 to 1.5% by mass; Mn in an amount of 0.7 to 1.5% by mass; Cr in an amount of 24 to 36% by weight; Mo in an amount of 3.5 to 4.5% by weight; Ni in an amount of 0.7 to 1.5% by weight; V in an amount of 1.5 to 2.5% by mass and W in an amount of 0.7 to 1.5% by mass.
    [0081] According to this configuration, the corrosion resistance, abrasion resistance and element resistance can be further improved.
    [0082] In the element of the present invention, the deposited metal may additionally contain P: 0.03 mass% or less, and S: 0.02 mass% or less.
    [0083] Preferably, in the element of the present invention, the deposited metal has a microstructure of
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    40/40 metal, where the matrix comprises a plurality of ferrite grains and a plurality of cementite grains are precipitated from ferrite bound grains. Most preferably, the metal microstructure of the deposited metal is a polycrystalline microstructure with a matrix formed as a ferrite phase, where cementite exists in crystal bound grains of ferrite crystal grains, while wrapping around the peripheries of the grains of ferrite crystal.
    [0084] According to this configuration, a plurality of cementite grains precipitated on the ferrite limit grains maintain the respective connections between the ferrite grains, with more preference, the cementite surrounds the ferrite, so that the ferrite microstructure as matrix it is less susceptible to cracking compared to an austenite microstructure and a martensite microstructure and the corrosion resistance of the element to acids is further enhanced.
    INDUSTRIAL APPLICABILITY [0085] As above, the deposited metal formed from the welding build-up material of the present invention is suitable for use in an apparatus that requires excellent corrosion resistance and abrasion resistance, such as a reactor sprayer or any another mechanical device for the treatment of an acidic substance or an object excavated from acidic soil and is of practical use for this purpose.
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    权利要求:
    Claims (13)
    [1]
    1 . Material in welding buildup characterized by to contain C: 0.2 to 1.5 % by mass, Si : 0.5 to 2% in mass, Mn: 0.5 to 2% by mass, Cr: 20 to 40% in bulk, Mo: 2 to 6% in pasta, Ni: 0.5 to 6% in bulk, V: 1 at 5% by mass and W: 0.5 to 5% in pasta, with the remaining being Fe and impurities inevitable. 2. Material in welding buildup, according to the claim 1 , featured per to contain: C in a
    amount from 0.6 to 0.8% by mass; Si in an amount of 0.7 to 1.5% by weight; Mn in an amount of 0.7 to 1.5% by weight; Cr in an amount of 24 to 36% by weight; Mo in an amount of 3.5 to 4.5% by weight; Ni in an amount of 0.7 to 1.5% by weight; V in an amount of 1.5 to 2.5% by weight and W in an amount of 0.7 to 1.5% by weight.
    [2]
    2/3
    [3]
    3/3 characterized by the fact that the deposited metal contains: C in an amount of 0.6 to 0.8% by weight; Si in an amount of 0.7 to 1.5% by weight; Mn in an amount of 0.7 to 1.5% by weight; Cr in an amount of 24 to 36% by weight; Mo in an amount of 3.5 to 4.5% by weight; Ni in an amount of 0.7 to 1.5% by weight; V in an amount of 1.5 to 2.5% by mass and W in an amount of 0.7 to 1.5% by mass.
    3. Welding accumulation material according to claim 1, characterized in that it also contains P: 0.03% by weight or less, and S: 0.02% by weight or less.
    [4]
    4. Welding accumulation material according to claim 1, characterized by containing one or more selected from the group consisting of Ti, Co, Cu, Zr, Nb, Pd, Ag, Sn, Hf, Ta, Pt, Au and Pb in a total amount of 15% by weight or less.
    [5]
    5. Metal deposited by accumulation of weld on a surface of a steel material serving as a base metal characterized by the fact that the deposited metal contains C: 0.2 to 1.5% by weight, Si: 0.5 to 2% in mass, Mn: 0.5 to 2% by mass, Cr: 20 to 40% by mass, Mo: 2 to 6% by mass, Ni: 0.5 to 6% by mass, V: 1 to 5% by mass and W: 0.5 to 5% by weight, with the remainder being Fe and unavoidable impurities.
    Petition 870180058798, of 07/06/2018, p. 48/51
    [6]
    Deposited metal according to claim 5, characterized in that it contains: C in an amount of 0.6 to 0.8% by weight; Si in an amount of 0.7 to 1.5% by weight; Mn in an amount of 0.7 to 1.5% by weight; Cr in an amount of 24 to 36% by weight; Mo in an amount of 3.5 to 4.5% by weight; Ni in an amount of 0.7 to 1.5% by weight; V in an amount of 1.5 to 2.5% by mass and W in an amount of 0.7 to 1.5% by mass.
    [7]
    7. Deposited metal according to claim 5, characterized in that it also contains P: 0.03% by weight or less, and S: 0.02% by weight or less.
    [8]
    8. Deposited metal, according to claim 5, characterized by containing one or more selected from the group consisting of Ti, Co, Cu, Zr, Nb, Pd, Ag, Sn, Hf, Ta, Pt, Au and Pb in a total amount of 15% by mass or less.
    [9]
    9. Deposited metal according to claim 5, characterized by the fact that it has a metal microstructure, where the matrix comprises a plurality of ferrite grains, and a plurality of cementite grains are precipitated from ferrite bound grains.
    [10]
    10. Element characterized by comprising a steel material that serves as a base metal and a metal deposited by accumulation of weld on a surface of the steel material, where the deposited metal contains C: 0.2 to 1.5% by mass , Si: 0.5 to 2% by mass, Mn: 0.5 to 2% by mass, Cr: 20 to 40% by mass, Mo: 2 to 6% by mass, Ni: 0.5 to 6% by weight mass, V: 1 to 5% by mass and W: 0.5 to 5% by mass, with the remainder being Fe and unavoidable impurities.
    [11]
    11. Element according to claim 10,
    Petition 870180058798, of 07/06/2018, p. 49/51
    [12]
    12. Element according to claim 10, characterized by the fact that the deposited metal additionally contains P: 0.03% by weight or less, and S: 0.02% by weight or less.
    [13]
    13. Element according to claim 10, characterized by the fact that the deposited metal has a metal microstructure, where the matrix comprises a plurality of ferrite grains, and a plurality of cementite grains are precipitated from limit grains of ferrite.
    Petition 870180058798, of 07/06/2018, p. 50/51
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    法律状态:
    2018-04-10| B06A| Notification to applicant to reply to the report for non-patentability or inadequacy of the application [chapter 6.1 patent gazette]|
    2018-07-31| B09A| Decision: intention to grant [chapter 9.1 patent gazette]|
    2018-09-25| B16A| Patent or certificate of addition of invention granted|Free format text: PRAZO DE VALIDADE: 20 (VINTE) ANOS CONTADOS A PARTIR DE 28/09/2011, OBSERVADAS AS CONDICOES LEGAIS. |
    优先权:
    申请号 | 申请日 | 专利标题
    JP2010222861|2010-09-30|
    PCT/JP2011/005449|WO2012042861A1|2010-09-30|2011-09-28|Surfacing material, deposited metal, and member involving deposited metal|
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