KR20150119181A - Buildup Welding Material, Straightening Roll, Guide Roll, Transporting Roll, and Anvil - Google Patents

Abstract

It is an object of the present invention to provide an additional welding material capable of suppressing deterioration of heat resistant cracking property while adding at least one kind of carbide selected from WC, CrC and NbC having excellent abrasion resistance to a predetermined Ni-based alloy. The welding material of the present invention is composed of a Ni-based alloy and a mixed carbide. The Ni-based alloy contains 0.1% or less of C, 10 to 15% of Cr, 8 to 15% of Mo, % Or less of Co, 15% or less of Co, 1 to 5% of Al, 1 to 5% of Ti and 0.01 to 0.1% of N and the balance Ni and inevitable impurities. % / 25 + W% / 31? 1, and the mixed carbide is composed of at least one of a first carbide of WC, NbC, VC and CrC and a second carbide of TiC, Wherein the first carbide is 5 to 50% and the second carbide is 3 to 30%, wherein the total amount of the Ni-based alloy and the mixed carbide is 100%, and the sum of the first and second carbides The amount is 10 to 60%.

Description

[0001] The present invention relates to a welding material, a correction roll, a guide roll, a conveying roll, and an anvil,

The present invention relates to a welding material for superimposing which has excellent heat-resistant cracking resistance and wear resistance at high temperature.

The steelworks is provided with various members requiring heat-resisting cracking and abrasion resistance at a high temperature region such as a continuous casting roll. Patent Document 1 discloses a ferritic stainless steel comprising 0.1% or less of C, 10-15% of Cr, 8-15% of Mo, 15% or less of Co, 5% or less of W, , And the remainder Ni, is disclosed.

The use of the welding material for continuous casting addition of Patent Document 1 shows excellent heat-resistant cracking property as a continuous casting roll. In a severe use environment, the heat-resistant cracking property of the base component is high, So that it is concentrated in the heat cracked portion where there is little thermal stress to be applied thereafter, and as a result, the number of thermal cracks is small, but it may become a deep crack. Such deep cracks lead to delamination of the overlapped layer, and thus there is a problem that early repair is required.

In order to solve the above-mentioned problems, Patent Document 2 discloses a ferritic stainless steel which contains 0.1% or less of C, 10 to 15% of Cr, 8 to 15% of Mo, 5% or less of W, 15% 33% + Mo% / 25 + W% / 31%, and the balance of Ni and inevitable impurities, and contains Al: 1 to 5%, Ti: 1 to 5% 1 < / RTI > for a continuous casting roll.

Patent Document 2 discloses that TiN is dispersed in the additional layer by containing a predetermined amount of Ti and N and this TiN becomes a starting point of thermal cracks generated during use of the continuous casting roll as a stress concentration source, And as a result, the thermal stress is relaxed by the microcracks, whereby it is described that large cracking and peeling of the surface layer, which is a cause of breakage of the continuous casting roll, can be suppressed.

Prior art literature

(Patent Literature)

Patent Document 1: JP-A-2005-144488

Patent Document 2: JP-A-2007-136509

In recent years, it has been demanded that the abrasion resistance is further improved in a continuous casting roll or the like. In general, as a method for improving wear resistance, a method of adding at least one kind of carbide among WC, CrC and NbC to a welding material for addition is known. However, when the carbide such as WC is added in the constitution of the above-mentioned Patent Document 2, Ti contained in the Ni-based alloy and C such as added WC are added thereto. In response to the welding, TiC is formed, The contained Ti content is lowered. When the Ti content is lowered, there is a possibility that the effect of making the thermal cracking finer by making the TiN a thermal stress concentration source may not be obtained (see paragraph 0019 of the specification of Patent Document 2). On the other hand, if the WC or the like is removed, there is a possibility that the improvement of the wear resistance may not be obtained.

Therefore, the present invention provides a welding material for an overlay which can suppress the deterioration of heat-resistant cracking property while adding at least one kind of carbide selected from WC, CrC and NbC excellent in wear resistance to the Ni-based alloy described in Patent Document 2 .

In order to solve the above problems, the present invention provides, as one aspect, (1) a welding material comprising Ni-based alloy and mixed carbide, wherein the Ni-based alloy contains 0.1% or less of C, 10 to 15% of Mo, 8 to 15% of W, 5% or less of W, 15% or less of Co, 1 to 5% of Al, 1 to 5% of Ti and 0.01 to 0.1% of N, 33 + Mo% / 25 + W% / 31 1, and the mixed carbide is at least one of WC, NbC, VC, and CrC, 1 carbide and a second carbide of TiC, wherein the first carbide is 5 to 50%, and the second carbide is 5 to 50%, when the total amount of the Ni-based alloy and the mixed carbide is 100% 3 to 30%, and the total amount of the first and second carbides is 10 to 60%. The welding material is excellent in heat resistance and wear resistance at high temperature.

(2) A welding material comprising a Ni-based alloy and a composite carbide, wherein the Ni-based alloy contains 0.1% or less of C, 10 to 15% of Cr, And the balance Ni and inevitable impurities are contained in an amount of from 8 to 15%, W to 5%, Co to 15%, Al to 1 to 5%, Ti to 1 to 5% and N to 0.01 to 0.1% (V, Ti) C, (V, Ti) C, (V, Ti) C, (Nb, Cr, Ti) C, (W, Nb, Ti) C, (W, V, Ti) C, (W, Nb, V, Ti) C, (W, Nb, Cr, Ti) C, (Nb, V, Cr, Ti) C, (W, Ti) C satisfies a composition ratio corresponding to WC / TiC = 30/70 to 70/30, and (Nb, Ti) C is NbC (TiC) satisfies a composition ratio corresponding to VC / TiC = 30/70 to 70/30, and (V, Ti) Ti) C _{is, Cr 3 C 2 / TiC =} 30/70 ~ satisfies the composition ratio corresponding to 70/30, (W, Nb , Ti) C is, WC / NbC / TiC = 15 /15/70 ~ Composition equivalent to 40/30/30 (W, Cr, Ti) C satisfies a composition ratio corresponding to WC / VC / TiC = 15/15/70/40/30/30 and (W, V, Ti) _{, WC / Cr 3 C 2 /} TiC = 15/15/70 ~ 40/30 / satisfy the composition ratio equal to 30 and, (Nb, V, Ti) C is, NbC / VC / TiC = 15 /15 / and 70 to satisfy the composition ratio corresponding to 40/30/30, the composition corresponding to the (Nb, Cr, Ti) C _{is, NbC / Cr 3 C 2 /} TiC = 15/15/70 ~ 40/30/30 (V, Cr, Ti) C satisfies a composition ratio corresponding to VC / Cr ₃ C ₂ / TiC = 15/15/70/40/30/30, and (W, Nb, V , Ti) C satisfies a composition ratio corresponding to WC / NbC / VC / TiC = 10/10/10 / 70-30 / 20/20/30, WC / NbC / Cr ₃ C ₂ / TiC = satisfies 10/10/10 / 70-30 / 20/20/30 composition ratio corresponding to the, and, (Nb, V, Cr, Ti) C is, NbC / VC _{/ Cr 3 C 2 / TiC =} 10/10/10/70 ~ 30/20/20 / satisfy the composition ratio equal to 30, and (W, Nb, V, Cr, Ti) C is, WC / NbC / the _{VC / Cr 3 C 2 / TiC} = 10/10/10/10/60 ~ 15/15/15/15 / , and satisfy the composition ratio corresponding to 40, wherein the Ni-based alloy, in weight percent, and the repeat carbide When the total amount is 100%, the clothing carbide is a welding heat cracking resistance and an excellent wear resistance at high temperatures redundancy station, characterized in that 10% to 60%.

According to the invention of the commercial value (1), since the addition amount of the first carbide decreases by adding the first carbide and the second carbide, Ti contained in the Ni-based alloy reacts with C in the first carbide, It is possible to suppress the decrease of Ti in the film. As a result, the effect of making the thermal cracking finer by using TiN as a heat sink concentrating source can be obtained. By adding the second carbide, it is possible to suppress the deterioration of the wear resistance due to the decrease in the amount of the first carbide added. Further, according to the invention (2), heat-resisting cracking resistance and wear resistance can be achieved at the same time as in the invention of (1).

1 is a schematic view of a test apparatus for a hot wear test.
2 is a schematic view of a calibrator including a calibrating roll;
Fig. 3 is a schematic configuration diagram of a rolling facility B and a winding facility C; Fig.
4 is a plan view of the winding facility C;
Figure 5 is a schematic view of an anvil.

The welding material of the present invention can be used for coating the roll surface of a calibrating roll, a guide roll, and a conveying roll used at a high temperature. The over-welding material of the present invention can be used in an anvil used in forging (forging).

Figure 2 is a schematic view of a calibrator including a calibrating roll; The calibrator A includes an upper calibrating roll 11 and a lower calibrating roll 12. The calibrator A is installed behind the rolling equipment of the steel pipe P and forcibly bends the steel pipe P in a heated state and is sent from the rolling facility to the next process. The upper calibrating roll 11 and the lower calibrating roll 12 are opposed to each other in the vertical direction so that the steel pipe P and the like P are passed between the calibrating rolls 11 and 12, Can be calibrated. The overlay welding material of the present invention can be used to coat the roll surfaces of the calibration rolls 11,

Fig. 3 is a schematic configuration diagram of the rolling facility B and the winding facility C. The rolling facility B is constituted by arranging a plurality of roll groups 21 on the upper and lower sides sandwiching the conveying path of the steel sheet and arranging them in the conveying path. The roll group 21 is constituted by a work roll 21a, an intermediate roll 21b, and a backup roll 21c. The work roll 21a is sandwiched between the heated steel plates and rolled. The intermediate roll 21b suppresses deformation of the work roll 21a at the time of rolling. The guide rolls 22 are arranged along the conveying path of the steel sheet, and are provided at both ends in the width direction of the steel sheet, thereby guiding the steel sheet proceeding along the conveying path. The overlay welding material of the present invention can be used to cover the roll surface of the guide roll 22.

The rolled steel sheet (hereinafter referred to as rolled steel sheet) in the rolling facility B is conveyed to the winding facility C by the conveying roll 41. [ The additional welding material of the present invention can be used to coat the roll surface of the transport roll 41. [

Fig. 4 is a plan view of the winding facility C. Fig. The winding facility C is a device for rolling the rolled steel sheet fed from the rolling facility B into a roll shape. In the winding facility C, a guide liner 31 and a guide roll 32 are provided. The guide liner 31 and the guide roll 32 are disposed at both ends in the width direction of the steel sheet, thereby guiding the rolled steel sheet proceeding along the conveying path. The overlay welding material of the present invention can be used to coat the roll surface of the guide roll 32. [

Figure 5 is a schematic view of an anvil. The overlay welding material of the present invention can be used to coat the surface of an anvil used for free forging. Free forging is one of the processing methods for performing forging by interposing a heated metal material between upper and lower pairs of anvils 51 and 52 and pressing it.

The reasons for limiting the Ni-based alloy according to the present invention will be described below. On the other hand, the following% means mass%.

C: not more than 0.1%

C forms a carbide with Ti, Cr, Mo, W and the like in the crystal grain boundaries to strengthen the grain boundaries. However, when the content exceeds 0.1%, the Ti, Cr, Mo, and W concentrations in the particles are lowered and adversely affecting the proof stress and oxidation resistance, so the upper limit is set to 0.1%.

Cr: 10 to 15%

Cr is required at least 10% in order to ensure oxidation resistance at high temperature. However, if it exceeds 15%, a brittle intermetallic compound precipitates and the ductility decreases. Therefore, the range was set at 10 to 15%.

Mo: 8 to 15%

Mo is dissolved in the? -Phase and has the effect of improving the high-temperature proof stress and the effect of lowering the thermal expansion coefficient. In addition, it is an element having an effect of enhancing the corrosion resistance to fluorine contained in the mold powder. However, if it is less than 8%, the effect is not sufficient. On the other hand, if it exceeds 15%, a brittle intermetallic compound precipitates and the ductility decreases. Therefore, the range is set to 8 to 15%.

W: 5% or less

W is an element which is dissolved in the? -Phase and has the effect of improving the high-temperature proof stress and the effect of lowering the thermal expansion coefficient. However, if it exceeds 5%, a brittle intermetallic compound precipitates and the ductility decreases, so that the upper limit is set to 5%.

Co: 15% or less

Co is an element having an effect of improving ductility. However, if it exceeds 15%, the cost increases, and the upper limit is set to 15%.

Al: 1 to 5%

Al is an element that forms a γ 'phase and improves the ocular resistance. However, if it is less than 1%, the effect is not obtained, and if it exceeds 5%, the ductility deteriorates, so that the range is set to 1 to 5%.

Ti: 1-5%

Ti produces TiN, becomes a source of thermal stress concentration, and makes thermal cracks finer. In addition, it replaces Al in the? 'Phase to strengthen the?' Phase. However, if the effect is less than 1%, the effect is not sufficient. If it exceeds 5%, the ductility decreases. Therefore, the range is set to 1 to 5%. That is, the content of Ti in the Ni-based alloy is 5% upper limit, and when it exceeds 5%, the ductility is lowered.

N: 0.01 to 0.1%

N produces TiN, becomes a source of thermal stress concentration, and makes thermal cracks finer. However, when the content is less than 0.01%, the effect is insufficient. When the content exceeds 0.1%, blow holes are liable to be generated at the time of welding.

Cr% / 33 + Mo% / 25 + W% / 31 1

If the ratio of Cr% / 33 + Mo% / 25 + W% / 31 exceeds 1, a brittle intermetallic compound is produced and the ductility is lowered. Therefore, the upper limit was set to 1.

The mixed carbide added to the Ni-based alloy will be described. The mixed carbide is composed of one or more of a first carbide of WC, NbC, VC and CrC, and TiC (second carbide). Namely, the mixed carbide is composed of mixed carbide composed of WC and TiC, mixed carbide composed of NbC and TiC, mixed carbide composed of VC and TiC, mixed carbide composed of CrC and TiC, mixed carbide composed of WC, NbC and TiC, Mixed carbides made of CrC and TiC, mixed carbides made of WC, VC and TiC, mixed carbides made of NbC, VC and TiC, mixed carbides made of CrC, VC and TiC, mixed carbides made of WC, NbC, CrC and TiC, Mixed carbides composed of WC, NbC, VC and TiC, mixed carbides composed of WC, CrC, VC and TiC, and mixed carbides composed of WC, NbC, CrC, VC and TiC.

The first carbide is 5 to 50%, the second carbide is 3 to 30%, and the total amount of the first and second carbides is 5 to 50% when the total amount of the Ni-based alloy and the mixed carbide is 100% Is 10 to 60%. Here, the mixed carbide refers to a carbide obtained by granulating and sintering particles composed of a first carbide and particles composed of a second carbide, and bonding only surfaces to each other.

By adding the first carbide and the second carbide to the Ni-based alloy in the above-mentioned ratio, it is possible to suppress deterioration of ductility (lowering of heat-resistant cracking resistance) and deterioration of wear resistance of the overburden welding layer . Generally, when only a first carbide is added to a Ni-based alloy in a superimposed manner, the outer circumferential portion of the carbide particles is thermally melted and the hot melted element is contained in the Ni-based alloy excessively, Ti and C of the first carbide react to form TiC. As a result, the content of Ti in the Ni-based alloy is reduced and the amount of TiN produced becomes insufficient, so that an effect of making the thermal cracking finer by making TiN a thermal stress concentration source can not be obtained.

When TiC as the second carbide is added to the Ni-based alloy as in the present embodiment, a part of the TiC is thermally melted by heat-receiving the heat at the time of welding, and a part of the thermally melted TiC is mixed with C And TiC having excellent wear resistance is precipitated. In addition, the remaining TiC that has not been thermally melted at the time of over welding is not chemically reacted with the Ni-based alloy, but is precipitated as it is. Therefore, it is possible to suppress side effects, that is, deterioration of wear resistance, by reducing the addition amount of the first carbide. Further, a part of the thermally melted TiC binds with N in the Ni-based alloy to form TiN, which becomes a heat stress concentration source as described above, thereby enhancing heat resistance cracking resistance.

Further, by reducing the amount of the first carbide added, the amount of TiC produced by the reaction of Ti in the Ni-based alloy and C contained in the first carbide is reduced, so that Ti can be sufficiently left in the Ni-based alloy. As a result, the amount of TiN generated as a stress concentration source is increased, so that heat resistance cracking due to miniaturization of thermal cracking can be satisfied.

Here, if the amount of the first carbide added is less than 5%, the wear resistance of the overlapped welding layer becomes insufficient. If the addition amount of the first carbide exceeds 50%, Ti in the Ni-based alloy decreases and the heat-resistant cracking property can not be satisfied. Also, the amount of W or the like in the Ni-based alloy is excessively increased and the ductility is lowered.

If the addition amount of the second carbide is less than 3%, the effect of suppressing the decrease in the amount of Ti contained in the Ni-based alloy becomes insufficient. When the added amount of the second carbide exceeds 30%, the carbide grows and cracks are generated. That is, the specific gravity of the second carbide is about 1/2 to 1/4 of that of the first carbide, and when the volume ratio is 2 to 4 times, the cracks are generated. The total amount of the first and second carbides is 10 to 60%. When the total amount of the first and second carbides exceeds 60%, Ti and N in the Ni-based alloy are so small that TiN as a stress concentration source can not be sufficiently generated in the beginning.

The double-carbide added to the Ni-based alloy will be described. (W, Ti) C, (Nb, Ti) C, (V, Ti) C, (Cr, Ti) C, (W, Cr, Ti) C, (Nb, V, Ti) C, (Nb, Cr, Ti) C, N, Cr, Ti) C, (Nb, V, Cr, Ti) C and (W, Nb, V, Cr, Ti) C.

These polycarbonates can be produced by the martram process. The martram method is a method in which a raw material composed of an Fe-carbide-forming metal (or Fe + carbide-forming metal) + C is mixed with a molten metal bath at a high temperature (for example, , Ni, Cu, Al, and the like), followed by acid treatment, followed by decomposition of carbides other than Fe in addition to Fe, followed by water washing / Sieve analysis and non-gravity casting to obtain a high-quality target carbide and at the same time to separate and remove impurities, followed by further drying and sieving analysis to obtain a desired carbide.

(W, Ti) C, which satisfies the composition ratio corresponding to WC / TiC = 30/70 to 70/30 in mass% as a result of variously changing the kind and composition of the blended raw materials by the above- (Nb, Ti) C satisfying a composition ratio corresponding to NbC / TiC = 30 / 70-70 / 30 and (V, Ti) satisfying a composition ratio corresponding to VC / TiC = 30 / 70-70 / corresponding to _{C, Cr 3 C 2 / TiC} = 30/70 ~ 70 / satisfying the composition ratio corresponding to 30 (Cr, Ti) C, WC / NbC / TiC = 15/15/70 ~ 40/30/30 (W, V, Ti) C, WC (W, V, Ti) C satisfying the composition ratio satisfying the composition ratio of WC / VC / TiC = 15/15/70/40/30/30 satisfying the composition ratio (W, Cr, Ti) C, NbC / VC / TiC = 15/15/70/40/30/30 satisfying the composition ratios corresponding to Cr ₃ C ₂ / TiC = satisfying a composition ratio equivalent to 30/30 (Nb, V, Ti) C, NbC / Cr 3 C 2 / TiC = 15/15/70 ~ 40/30 / that satisfies the composition ratio corresponding to 30 (Nb , Cr, Ti) C, VC / Cr 3 C 2 / TiC = 15/15/70 ~ 40/30 / that satisfies the mole fraction corresponding to the 30 (V, Cr, Ti) C, WC / NbC / VC / TiC = 10/10/10/70 ~ 30/20/20/30 (W, Nb, V, Ti ) satisfying the composition ratio of C, WC / NbC / Cr satisfying a composition ratio equivalent to _{3 C 2 / TiC = 10/} 10/10/70 ~ 30/20/20/30 for (W, Nb, Cr, Ti ) C, NbC / VC / Cr 3 C 2 / TiC = 10/10/10/70 ~ 30/20/20 / that satisfies the composition ratio corresponding to 30 (Nb, V (W, Cr, Ti) C and WC / NbC / VC / Cr ₃ C ₂ / TiC = 10/10/10/10 / 60-15 / 15/15 / Nb, V, Cr, Ti) C could be produced.

When the total amount of the Ni-based alloy and the composite carbide is 100% by mass, the content of the composite carbide is 10 to 60%. By adding the composite carbide to the Ni-based alloy at this ratio, it is possible to suppress the deterioration of the ductility (lowering of the heat-resistant cracking resistance) and the deterioration of the wear resistance of the overlapped welded layer, as demonstrated in Examples to be described later. Generally, when only a large amount of carbides composed of W, Nb, V and Cr is added to a Ni-based alloy and are welded together, the outer circumferential portion of the carbide particles is thermally melted and the hot melted element is excessively contained in the Ni- , Ti contained in the Ni-based alloy reacts with C of carbide composed of W, Nb, V, and Cr to form TiC. As a result, the content of Ti contained in the Ni-based alloy decreases, and the amount of TiN generated becomes insufficient. Thus, the effect of making the thermal cracking source by making TiN a thermal stress concentration source is not obtained.

When a double-carbide containing Ti is added to a Ni-based alloy as in the present embodiment, Ti and C are thermally melted by heat treatment at the time of welding, and a part of the thermally melted Ti is mixed with the Ni- C, TiC having excellent abrasion resistance is precipitated. In addition, the remaining Ti and C, which have not been thermally melted at the time of over welding, do not chemically react with the Ni-based alloy and precipitate as TiC excellent in abrasion resistance. Therefore, it is possible to suppress a side effect, that is, a deterioration in wear resistance, caused by reducing the amount of carbide formed of W, Nb, V and Cr. In addition, a part of the thermally melted Ti bonds with N in the Ni-based alloy to generate TiN. Such TiN becomes a heat stress concentration source as described above, so that the heat resistance cracking property becomes high.

Further, by decreasing the addition amount of carbide consisting of W, Nb, V and Cr, the amount of TiC generated in response to the reaction of Ti in the Ni-based alloy and C contained in the carbide composed of W, Nb, V and Cr decreases Therefore, Ti can be sufficiently left in the Ni-based alloy. As a result, the amount of TiN generated as a stress concentration source is increased, so that heat resistance cracking due to miniaturization of thermal cracking can be satisfied.

Examples Next, the present invention will be described in more detail with reference to Examples. Various examples and comparative examples were prepared and the abrasion resistance and the heat cracking resistance of the overlapped welding layer were evaluated. The abrasion resistance is determined by welding the SS400 material in various examples and comparative examples shown in Tables 1 and 2, and using the test pieces taken out from the material as a counterpart, the hot wear test is performed in the apparatus shown in Fig. 1 . More specifically, the abrasion resistance of the test piece was evaluated by measuring the amount of abrasion of the test piece under a constant load, constant time press, and SKD-11 (φ30-40L / hardness (Hs) 80 to 85). When the wear loss was over 100 mg, the abrasion resistance was evaluated as " poor ". When the weight loss was less than 50 mg and less than 100 mg, the abrasion resistance was evaluated as good. When the wear loss was less than 50 mg, the abrasion resistance was evaluated to be very good and rated as?.

The heat-cracking resistance was evaluated by a heat-check test. The rolled welded roll was rotated at a rotational speed of 1.44 rpm and heated by a gas burner from above, cooling water was sprayed from the bottom, and heated at 400 DEG C and 200 DEG C The thermal cycle of cooling was applied 5,000 times. Thereafter, the cross section (150 mm x 40 mm, four cross sections) of the roll surface portion was microscopically observed and evaluated by the maximum crack depth. When the maximum crack depth was 6 mm or more, the heat cracking resistance was evaluated as "poor". When the maximum crack depth was 5 mm or more and less than 6 mm, the heat-resistant cracking resistance was evaluated as good. When the maximum crack depth was less than 5 mm, the heat-resisting cracking property was evaluated as " Excellent "

Table 1 shows the test results when welding is performed using an Ni-based alloy and an additive welding material composed of mixed carbides. Table 2 shows test results when Ni-based alloys and double-carbide welding materials are used. Table 3 shows the test conditions for the hot wear test. Ni alloy containing 0.05% of C, 13% of Cr, 11% of Mo, 2% of W, 10% of Co, 2% of A, 2% of Ti and 0.02% Ni and inevitable impurities were used.

[Table 1A]

[Table 1B]

[Table 1C]

[Table 1D]

[Table 1E]

[Table 2A]

[Table 2B]

[Table 2C]

[Table 2D]

[Table 2E]

[Table 2F]

[Table 2G]

[Table 2H]

[Table 2I]

[Table 2J]

[Table 2K]

[Table 2L]

[Table 2M]

[Table 2N]

[Table 3]

As shown in Tables 1A to 1E, it was found that the deterioration of the abrasion resistance due to the reduction of the amount of the first carbides (WC, NbC, CrC and VC) can be suppressed by adding the second carbide (TiC). That is, when the first carbide (WC, NbC, CrC, VC) is contained in an amount of 5 mass% or more, by adding the second carbide (TiC), it is possible to suppress the wear loss to 100 mg or less I could.

(W, Ti) C and NbC / TiC = 30/70 to 70/30 satisfying the composition ratio corresponding to WC / TiC = 30/70 to 70/30 as shown in Tables 2A to 2E (V, Ti) C, Cr ₃ C ₂ / TiC = 30/70 to 70 (Nb, Ti) C satisfying the composition ratios corresponding to VC / TiC = 30/70 to 70/30 (W, Nb, Ti) C (Cr, Ti) C satisfying the composition ratio corresponding to WC / NbC / TiC = 15/15/70/40/30/30, (W, V, Ti) C, WC / Cr ₃ C ₂ / TiC = 15/15/70 to 30/30 satisfying the composition ratios corresponding to WC / VC / TiC = 15/15/70/40/30/30. (W, Cr, Ti) C satisfying the composition ratio corresponding to 40/30/30 and NbC / VC / TiC = 15/15/70/40/30/30 satisfying the composition ratio corresponding to NbC / (Nb, Cr, Ti) C, VC / Cr ₃ C ₂ / TiC which satisfy the composition ratios corresponding to NbC / Cr ₃ C ₂ / TiC = 15/15/70/40/30/30. (V, Cr, Ti) C and WC / NbC / VC / TiC = 10/10/10/70/30/20/30, (W, Nb, V, Ti) C, WC / NbC / Cr ₃ C ₂ (W, Nb, Cr, Ti) C, NbC / VC / Cr ₃ C ₂ / TiC = 10/30/20/30/30, 10/10 / 70-30 / 20/20 / that satisfies the composition ratio corresponding to 30 (Nb, V, Cr, Ti) C, WC / NbC / VC / Cr 3 C 2 / TiC = 10/10/10 (W, Nb, V, Cr, and Ti) C satisfying a compositional ratio corresponding to 10/60 to 15/15/15/15/40 in an amount of 10 mass% or more , It was found that the weight loss can be suppressed to 100 mg or less, which is a passing criterion.

Here, it was impossible to make a polycarbonate having a composition ratio exceeding the above range in the beginning. The double-carbide according to Claim 2 of the present application only defines a manufacturable polycarbonate that satisfies desired wear resistance and heat-resisting cracking property.

As shown in Table 1A, in Comparative Example 2 in which only the first carbide was added to the Ni-based alloy, the amount of Ti in the matrix metal decreased and the depth of cracks increased. On the other hand, in the present embodiment, the amount of Ti in the matrix metal is hardly lowered, and the crack depth is smaller than that of the comparative material. For example, as shown in Examples 1 to 8 of Table 1A, when the amount of the first carbide added is smaller than that of Comparative Example 2, the heat-resistant cracking property is improved. That is, since the amount of TiC generated by the reaction between Ti in the Ni-based alloy and C contained in the first carbide is reduced by reducing the amount of the first carbide added, Ti can be sufficiently left in the Ni-based alloy, It is considered that the amount of TiN as a stress concentration source is increased. Examples 14 to 16 of Table 1A, Examples 19 to 22 of Table 1A, Examples 25 to 28 of Table 1A, Examples 31 to 37 of Table 1B, Examples 43 to 49 of Table 1B, Examples 55 to 61, Examples 67 to 73 of Table 1C, Examples 79 to 85 of Table 1C, Examples 91 to 97 of Table 1C, Examples 103 to 109 of Table 1D, Examples 115 to 121 of Table 1D, Similar results were obtained in Examples 127 to 133 of Table 1E and 139 to 145 of Table 1E.

Also, as shown in Examples 9 to 13 in Table 1A, even when a large amount of the first carbide is added (the addition amount of the first carbide is 50% or less), by adding TiC as the second carbide, It is considered that TiN as a circle is generated. Examples 17 to 18 of Table 1A, 23 to 24 of Table 1A, 29 to 30 of Table 1A, Examples 38 to 42 of Table 1B, Examples 50 to 54 of Table 1B, Examples 62 to 66 of Table 1B, Examples 74 to 78 of Table 1C, Examples 86 to 90 of Table 1C, Examples 98 to 102 of Table 1C, Examples 110 to 114 of Table 1D, Examples 122 to 126 of Table 1D, Examples of Table 1D 134 to 138, and Examples 146 to 150 of Table 1E, the same results were obtained.

With reference to Comparative Example 5 in Table 1A, when the WC as the first carbide exceeded 50%, the maximum crack depth increased to 6.3 mm. Referring to Comparative Example 8 in Table 1A, the maximum uniform depth increased to 6.5 mm when NbC as the first carbide exceeded 50%. Referring to Comparative Example 11 in Table 1A, when the CrC as the first carbide exceeded 50%, the maximum crack depth increased to 6.6 mm. Referring to Comparative Example 14 in Table 1A, when the VC as the first carbide exceeds 50%, the maximum crack depth increases to 7.0 mm. Referring to Comparative Example 17 of Table 1B, when the total amount of WC and NbC as the first carbide exceeded 50%, the maximum crack depth increased to 6.6 mm. Referring to Comparative Example 19 in Table 1B, when the total amount of WC and CrC as the first carbide exceeded 50%, the maximum crack depth increased to 6.5 mm. Referring to Comparative Example 21 in Table 1B, when the total amount of WC and VC as the first carbide exceeded 50%, the maximum crack depth increased to 6.7 mm. Referring to Comparative Example 23 in Table 1C, when the total amount of NbC and CrC as the first carbide exceeded 50%, the maximum crack depth increased to 6.4 mm. With reference to Comparative Example 25 in Table 1C, when the total amount of NbC and VC as the first carbide exceeded 50%, the maximum crack depth increased to 6.7 mm. Referring to Comparative Example 27 in Table 1C, when the total amount of CrC and VC as the first carbide exceeded 50%, the maximum crack depth increased to 6.8 mm. Referring to Comparative Example 29 in Table 1D, the maximum crack depth increased to 6.5 mm as the total amount of WC, NbC, and CrC as the first carbide exceeded 50%. Referring to Comparative Example 31 of Table 1D, the maximum crack depth was increased by 6.4 mm when the total amount of WC, NbC and VC as the first carbides exceeded 50%. Referring to Comparative Example 33 in Table 1D, the maximum crack depth increased to 6.9 mm when the total amount of WC, CrC, and VC as the first carbides exceeded 50%. Referring to Comparative Example 35 of Table 1E, when the total amount of WC, NbC, CrC, and VC as the first carbides exceeded 50%, the maximum crack depth increased to 6.9 mm. From this, it is considered that when the amount of the first carbide added exceeds 50%, Ti in the Ni-based alloy excessively decreases and the heat-resistant cracking property is remarkably lowered. Further, by limiting the addition amount of the predetermined polycarbonate to 60 mass% or less, the heat resistance cracking resistance can be suppressed to 6 mm or less, which is the acceptance criterion.

Claims (7)

Ni alloy, and a mixed carbide,
Wherein the Ni-based alloy contains 0.1 to 10% of C, 10 to 15% of Cr, 8 to 15% of Mo, 5% or less of W, 15% or less of Co, 33% + Mo% / 25 + W% / 31? 1, and the balance of Ni and inevitable impurities.
Wherein the mixed carbide is composed of at least one of a first carbide of WC, NbC, VC, and CrC, and a second carbide of TiC,
Wherein the first carbide is 5 to 50% and the second carbide is 3 to 30% when the total amount of the Ni-based alloy and the mixed carbide is 100% by mass%, the first and second carbides Is 10 to 60%. The weld material for superimposing is excellent in heat-resistant cracking resistance and wear resistance at high temperature. Ni-based alloy, and a composite carbide,
Wherein the Ni-based alloy contains 0.1 to 10% of C, 10 to 15% of Cr, 8 to 15% of Mo, 5% or less of W, 15% or less of Co, 33% + Mo% / 25 + W% / 31? 1, and the balance of Ni and inevitable impurities.
(W, Ti) C, (Nb, Ti) C, (V, Ti) C, (Cr, Ti) C, (W, Cr, Ti) C, (Nb, V, Ti) C, (Nb, Cr, Ti) C, (Nb, Cr, Ti) C, (Nb, V, Cr, Ti) C,
(W, Ti) C satisfies a composition ratio corresponding to WC / TiC = 30/70 to 70/30 in terms of mass%, and (Nb, Ti) C satisfies NbC / TiC = 30/70 to 70/30 (V, Ti) C satisfies a composition ratio corresponding to VC / TiC = 30/70 to 70/30 and (Cr, Ti) C satisfies a composition ratio of Cr ₃ C ₂ / TiC = (W, Nb, Ti) C satisfies a composition ratio corresponding to WC / NbC / TiC = 15/15/70 to 40/30/30, W, V, Ti) C is WC / VC / TiC = 15/ 15/70 ~ 40/30 / satisfy the composition ratio equal to 30 and, (W, Cr, Ti) C is WC / Cr ₃ C ₂ / (Nb, V, Ti) C satisfies NbC / VC / TiC = 15/15/70/40/30/30 and satisfies the mole fraction of, (Nb, Cr, Ti) C satisfies the mole fraction corresponding to the _{NbC / Cr 3 C 2 / TiC} = 15/15/70 ~ 40/30/30, and (V, Cr, (W, Nb, V, Ti) C satisfies a composition ratio corresponding to VC / Cr ₃ C ₂ / TiC = 15/15/70/40/30/30, and WC / NbC / VC / (W, Nb, Cr, Ti) C satisfies a composition ratio corresponding to TiC = 10/10/10 / 70-30 / 20/20/30 and WC / NbC _{/ Cr 3 C 2 / TiC =} 10/10/10/70 ~ 30/20/20 / , and satisfies the mole fraction equal to 30, (Nb, V, Cr , Ti) C is NbC / VC / Cr ₃ C _{2 / TiC = 10/10/} 10/70 ~ 30/20/20 / satisfy the composition ratio equal to 30, and (W, Nb, V, Cr, Ti) C is _{WC / NbC / VC / Cr 3} C ₂ / TiC = 10/10/10/10 / 60-15 / 15/15/15/40,
Wherein the composite carbide is 10% to 60% by mass when the total amount of the Ni-based alloy and the composite carbide is taken as 100%, wherein the composite carbide has a heat-resisting cracking property and an abrasion resistance at high temperature, . A calibrating roll for calibrating a bending of a heated steel tube,
Wherein the roll surface of the calibrating roll is welded in an overlapping manner by the overlap welding material according to claim 1 or 2. As a guide roll used in a rolling facility for rolling a heated steel sheet,
Wherein the roll surface of the guide roll is welded in an overlapping manner by the overlap welding material according to claim 1 or 2. As a guide roll used in a winding apparatus for winding a rolled rolled steel sheet in a rolling facility,
Wherein the roll surface of the guide roll is welded in an overlapping manner by the overlap welding material according to claim 1 or 2. As a conveying roll for conveying rolled rolled steel sheets to a winding facility in a rolling facility,
And the roll surface of the conveying roll is welded in an overlapping manner by the overlap welding material according to claim 1 or 2. As an anvil used in free forging,
Characterized in that the surface of the anvil is over-welded by the over-welding material according to claim 1 or 2.

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