JP2005330569A - Method for forming sprayed coating and laminate - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a method for adequately forming a thermal-sprayed film superior in impact peeling resistance, and to provide a layered body provided with the thermal-sprayed film superior in impact peeling resistance. <P>SOLUTION: The layered body comprises: a substrate having Vickers hardness in between 500 and 600; an undercoat layer formed on the substrate; and a top coating layer formed on the undercoat layer. When the substrate has the Vickers hardness of 500 or lower, the undercoat layer has the Vickers hardness higher than that of the substrate but lower than 810. When the substrate has the Vickers hardness of 600 or lower, the undercoat layer has the Vickers hardness lower than that of the substrate but higher than 230. The top coating layer is the thermal-sprayed film formed of a thermal spraying material consisting of a cermet powder, or a mixed powder of a metal and cermet, by thermal spraying. The thermal spraying material to be used preferably contains tungsten carbide. <P>COPYRIGHT: (C)2006,JPO&NCIPI

Description

  The present invention relates to a method for forming a thermal spray coating and a laminate including the thermal spray coating.

  In addition to good wear resistance, the thermal spray coating that is provided on parts used under harsh conditions, such as the blades of crushers and the tip parts of excavators, has good impact resistance. It is required to provide.

  It is known that the impact resistance of a thermal spray coating is affected by the hardness of a substrate on which the thermal spray coating is provided. If the substrate is deformed when an impact is applied to the sprayed coating from the outside, the sprayed coating is cracked or peeled unless the sprayed coating is deformed following the deformation of the substrate. In other words, when the hardness of the thermal spray coating is high and it is difficult to deform the thermal spray coating following the deformation of the base material, the thermal spray coating is more difficult to deform, that is, the higher the hardness of the base material. Therefore, the impact peel resistance is improved accordingly. However, even if the hardness of the base material is too high, the impact peel resistance of the thermal spray coating is lowered. This is because the anchor effect between the substrate and the thermal spray coating is weakened as the hardness of the substrate increases.

  Non-Patent Document 1 reports a technique for improving the impact peel resistance of a thermal spray coating by increasing the hardness of the substrate in advance by heat treatment before forming the thermal spray coating. According to the method of increasing the hardness of the substrate by heat treatment, it is not necessary to prepare a substrate having a high hardness. A hard substrate is generally expensive. However, this heat treatment is not easy when the base material is large, and costs high. Also, depending on the material of the base material, the hardness of the base material may not increase even if heat treatment is performed.

In addition, the characteristics required for various parts vary depending on the application, and the material of the base material used is often limited by the application. Since the impact peel resistance of the thermal spray coating may be influenced by the material of the base material, the thermal spray coating cannot often exhibit sufficient impact resistance resistance due to the limitation of the material of the base material.
Yoichi Matsubara, Reiko Takara, Effect of substrate hardness on the destruction of WC-Co sprayed coatings in process rolls, Journal of High Temperature Society, November 2003, Vol. 29, Supplement, p. 241-246

  The present invention has been made in view of such circumstances, and its purpose is to form a thermal spray coating capable of satisfactorily forming a thermal spray coating excellent in impact peel resistance, and thermal spray excellent in impact peel resistance. It is providing the laminated body provided with the membrane | film | coat.

  In order to achieve the above object, according to the first aspect of the present invention, there is provided a base material having a Vickers hardness of 500 or less, a first film provided on the base material, and a top surface of the first film. And a thermal spray coating as a second coating provided on the substrate, wherein the first coating has a Vickers hardness higher than that of the substrate and lower than 810. A laminate is provided.

  In the invention described in claim 2, as a base material having a Vickers hardness of 600 or more, a first film provided on the base material, and a second film provided on the first film And a thermal spray coating, wherein the first coating has a Vickers hardness lower than that of the substrate and higher than 230.

  The invention according to claim 3 is the laminate according to claim 1 or 2, wherein the second coating is formed by thermal spraying of a thermal spray material made of cermet powder or a mixed powder of cermet and metal. And the thermal spray material contains tungsten carbide.

  In the invention according to claim 4, the step of forming the first film on the substrate having a Vickers hardness of 500 or less, and the second film on the first film formed on the substrate. A method of forming a thermal spray coating as a coating, wherein the first coating has a Vickers hardness higher than that of the substrate and lower than 810. A method for forming a film is provided.

  In the invention according to claim 5, the step of forming the first film on the substrate having a Vickers hardness of 600 or more, and the second film on the first film formed on the substrate. A method of forming a thermal spray coating as a coating, wherein the first coating has a Vickers hardness lower than that of the substrate and higher than 230. A method for forming a film is provided.

  ADVANTAGE OF THE INVENTION According to this invention, the laminated body provided with the formation method of the thermal spray coating which can form the thermal spray coating excellent in the impact-peeling resistance favorably, and the thermal spray coating excellent in the impact-proof peeling property is provided.

Hereinafter, an embodiment of the present invention will be described.
The laminate according to the present embodiment is provided on a base material having a Vickers hardness of 500 or less or 600 or more, an undercoat layer (first film) provided on the base material, and the undercoat layer. And a thermal spray coating as a top coat layer (second coating). A laminated body is manufactured through the process of forming an undercoat layer on a base material, and the process of forming a topcoat layer on the undercoat layer formed on the base material.

  The undercoat layer may be formed by any of overlay welding, flame spraying, high-speed flame spraying, and plasma spraying, and is preferably formed by overlay welding or flame spraying. According to the overlay welding method or the flame spraying method, a dense undercoat layer can be formed at low cost.

  When the undercoat layer is formed by overlay welding, the welding material is melted and the molten welding material is deposited on the base material. The welding material used may be any of a wire, a rod, and powder. When depositing the welding material on the base material, the base material surface may be semi-melted by heat treatment. When a welding material is deposited on the semi-melted substrate surface, the adhesion between the undercoat layer and the substrate is improved.

  When the undercoat layer is formed by the flame spraying method, the sprayed material is melted or semi-molten, and the melted or semi-molten sprayed material is sprayed onto the substrate. The thermal spray material used may be any of a wire, a rod, and a powder. In the case of spraying a powdered thermal spray material by a flame spraying method, the particle size distribution of the powdered thermal spray material is desirably about 45 to 150 μm.

  The thermal spray material used when forming the undercoat layer by the flame spraying method may be a self-fluxing alloy. The self-fluxing alloy is obtained by adding boron and silicon to a nickel-based, nickel-chromium-based or cobalt-based alloy, and the thermal spray coating containing the self-fluxing alloy is defined in JIS H 8303.

  In particular, when a self-fluxing alloy is contained in the undercoat layer, it is preferable to subject the undercoat layer to a fusing treatment for heating the undercoat layer to a semi-molten state. When the undercoat layer is subjected to fusing treatment, the undercoat layer is densified. In addition, mutual diffusion occurs between the base material and the undercoat layer, and as a result, the undercoat layer is metallurgically bonded to the base material, improving the adhesion between the undercoat layer and the base material. To do. During the fusing treatment, the undercoat layer may be heated by a combustion flame of oxygen and acetylene, or may be heated together with the substrate in a heating furnace. The fusing treatment is preferably performed before the topcoat layer is formed on the undercoat layer.

  The porosity of the undercoat layer is desirably as low as possible. Specifically, the porosity of the undercoat layer is preferably 10% by volume or less, more preferably 5% by volume or less, and most preferably 0% by volume. When the porosity of the undercoat layer is too high, the deformation of the undercoat layer when the external impact is applied to the topcoat layer is not suppressed so much, and the impact peel resistance of the topcoat layer is greatly improved. There are things that do not.

  The thickness of the undercoat layer is preferably greater than 0.08 mm, more preferably greater than 0.15 mm, preferably 5 mm or less, more preferably 3 mm or less. When the thickness of the undercoat layer is too small, the deformation of the undercoat layer when the impact is applied from the outside to the topcoat layer is not suppressed so much, and the impact peel resistance of the topcoat layer is greatly improved. There are things that do not. If the thickness of the undercoat layer is too large, there is a disadvantage in terms of cost.

  When the Vickers hardness of the substrate is 500 or less, it is essential that the Vickers hardness of the undercoat layer is higher than the Vickers hardness of the substrate and lower than 810. On the other hand, when the Vickers hardness of the substrate is 600 or more, it is essential that the Vickers hardness of the undercoat layer is lower than the Vickers hardness of the substrate and higher than 230. In any case where the Vickers hardness of the substrate is 500 or less and 600 or more, the Vickers hardness of the undercoat layer is preferably greater than 260, more preferably greater than 350, preferably less than 780, more Preferably it is smaller than 680. When the Vickers hardness of the undercoat layer is too low or too high, the impact peel resistance of the topcoat layer may be lowered due to the undercoat layer. The reason why the impact peel resistance of the topcoat layer decreases when the Vickers hardness of the undercoat layer is too low is that the undercoat layer is deformed when an external impact is applied to the topcoat layer. The reason why the impact peel resistance of the topcoat layer decreases when the Vickers hardness of the undercoat layer is too high is that the anchor effect on the undercoat layer is weakened. The anchor effect is based on a mechanical engagement between the undercoat layer and the topcoat layer caused by the sprayed particles colliding with the undercoat layer when the topcoat layer is formed. The adhesion of the topcoat layer is improved.

  The top coat layer is a thermal spray coating, and is formed by any one of high-speed flame spraying methods such as HVOF (High Velocity Oxygen-Fuel) method and HVAF (High Velocity Air-Fuel) method, explosion spraying method, and cold spraying method. Preferably, it is more preferably formed by high-speed flame spraying or explosion spraying. When forming the topcoat layer, it is desirable that the flying speed of the sprayed particles, that is, the speed of the molten or semi-molten sprayed material ejected from the sprayer exceeds 400 m / second. According to the high-speed flame spraying method, the explosion spraying method, and the cold spray method, there is a high possibility that the flying speed of the sprayed particles exceeds 400 m / second, and the high-speed flame spraying method and the explosion spraying method have particularly high film forming ability. When the spray speed of the spray particles is 400 m / sec or less, the anchoring effect of the topcoat layer with respect to the undercoat layer is weakened, and the impact peel resistance of the topcoat layer may not be improved so much.

  The thermal spray material used when forming the topcoat layer is preferably cermet powder or a mixed powder of cermet and metal. It is desirable that the cermet powder and the mixed powder used as the thermal spray material contain tungsten carbide. The amount of tungsten carbide contained in each of the cermet powder and the mixed powder is preferably 50% by weight or more. The mixed powder of cermet and metal may be a mixed powder of cermet and metal containing tungsten carbide as disclosed in, for example, Japanese Patent Application Laid-Open No. 2002-220652.

  The cermet containing 50% by weight or more of tungsten carbide contains “WC / 12Co” which is a cermet containing 12% by weight of cobalt and the balance of tungsten carbide, 17% by weight of cobalt and the balance of tungsten carbide. The cermet “WC / 17Co”, the cermet “WC / 10Co / 4Cr” containing 10 wt% cobalt and 4 wt% chromium and the balance tungsten carbide, 20 wt% chromium carbide and 7 wt% "WC / 20CrC / 7Ni", which is a cermet containing nickel and the balance tungsten carbide, is known. Any of these may be used as the cermet in the thermal spray material.

  The thickness of the top coat layer is preferably greater than 40 μm, more preferably greater than 70 μm, preferably 800 μm or less, more preferably 500 μm or less. A topcoat layer that is too thin does not have very high impact peel resistance. When the thickness of the top coat layer is too large, there is a disadvantage in terms of cost.

This embodiment has the following advantages.
-When the Vickers hardness of the substrate is 500 or less, the amount of deformation of the undercoat layer when an external impact is applied to the topcoat layer provided on the undercoat layer having a hardness higher than that of the substrate is The amount of deformation of the base material when an external impact is applied to the top coat layer directly provided on the base material is small. That is, by providing the topcoat layer on the undercoat layer having a hardness higher than that of the base material, the deformation of the substrate that causes the topcoat layer to peel off is suppressed. Therefore, even if the topcoat layer provided on the undercoat layer has a high hardness, the topcoat layer has higher impact peel resistance than the topcoat layer provided directly on the substrate.

  -The Vickers hardness of an undercoat layer when the Vickers hardness of a base material is 500 or less is lower than 810. Therefore, since the Vickers hardness of the undercoat layer is too high, the anchor effect is reduced, and as a result, the situation in which the impact peel resistance of the topcoat layer is lowered due to the undercoat layer does not occur.

  -The Vickers hardness of the undercoat layer when the Vickers hardness of the substrate is 600 or more is higher than 230. Therefore, since the Vickers hardness of the undercoat layer is too low, the undercoat layer is deformed when an external impact is applied to the topcoat layer. As a result, the impact resistance of the topcoat layer is reduced by the undercoat layer. However, there is no such thing as a decline.

  -The Vickers hardness of the undercoat layer when the Vickers hardness of the substrate is 600 or more is lower than the Vickers hardness of the substrate. Therefore, the anchor effect is reduced because the Vickers hardness of the undercoat layer is higher than the Vickers hardness of the base material, and as a result, the impact peel resistance of the topcoat layer is reduced due to the undercoat layer. Will never happen.

  -In this embodiment, the impact-peeling resistance of the topcoat layer is improved by providing an undercoat layer having a predetermined hardness between the base material and the topcoat layer. Therefore, an expensive base material with high hardness is not required, and there is no need to heat-treat the base material in order to increase the hardness of the base material. Further, the impact peel resistance of the topcoat layer can be improved almost without being affected by the material and size of the substrate.

  -When a top coat layer is formed by thermal spraying cermet powder or mixed powder of cermet and metal, a top coat layer having high wear resistance can be obtained. In particular, a top coat layer formed by thermal spraying a cermet powder or a mixed powder having a tungsten carbide content of 50% by weight or more has very high wear resistance.

  Next, the present invention will be described more specifically with reference to examples and comparative examples.

実施例１〜３３及び比較例１〜７において、基材をそれぞれ用意した。各基材の材質及びビッカース硬度は上記表１〜３の“基材”欄に示す通りである。基材の外径寸法はいずれも８０ｍｍ×８０ｍｍ×２０ｍｍである。実施例１〜３３及び比較例１，６，７においては、基材の上にアンダーコート層を形成し、さらにそのアンダーコート層の上にトップコート層を形成することにより積層体を作製した。比較例２，３においては、トップコート層の形成を省略して基材の上にアンダーコート層のみを形成することにより積層体を作製した。比較例４，５においては、アンダーコート層の形成を省略して基材の上に直接トップコート層を形成することにより積層体を作製した。

In Examples 1 to 33 and Comparative Examples 1 to 7, base materials were prepared. The material and Vickers hardness of each base material are as shown in the “Base material” column of Tables 1 to 3 above. The outer diameters of the base materials are all 80 mm × 80 mm × 20 mm. In Examples 1 to 33 and Comparative Examples 1, 6, and 7, a laminate was produced by forming an undercoat layer on a substrate and further forming a topcoat layer on the undercoat layer. In Comparative Examples 2 and 3, a laminate was produced by omitting the formation of the topcoat layer and forming only the undercoat layer on the substrate. In Comparative Examples 4 and 5, the formation of the undercoat layer was omitted, and the laminate was prepared by forming the topcoat layer directly on the substrate.

  In Examples 1 to 8, 10 to 33 and Comparative Examples 1, 2, 6, and 7, an undercoat layer was formed by flame spraying, and the formed undercoat layer was subjected to fusing treatment. In Example 9 and Comparative Example 3, an undercoat layer was formed by overlay welding. The thermal spray material or welding material used in forming the undercoat layer, and the Vickers hardness and thickness of the formed undercoat layer are as shown in the “undercoat layer” column of Tables 1 to 3. Further, the porosity of the undercoat layer measured using an image analysis processing apparatus “NSFJ1-A” manufactured by NSupport is 2% by volume or less.

  “A” in the “Undercoat” column is 14.0 wt% chromium, 4.0 wt% iron, 3.6 wt% silicon, 2.5 wt% boron, and 0.6 wt%. Represents "Ni-14.0Cr-4.0Fe-3.6Si-2.5B-0.6C", which is an alloy containing a large amount of carbon and the remaining nickel. “B” in the “Undercoat” column is 11.0 wt% chromium, 2.5 wt% iron, 3.0 wt% silicon, 2.3 wt% boron, and 0.4 wt%. Represents "Ni-11.0Cr-2.5Fe-3.0Si-2.3B-0.4C", which is an alloy containing a large amount of carbon and the remaining nickel. “C” in the “Undercoat” column is 17.0 wt% chromium, 4.0 wt% iron, 4.3 wt% silicon, 3.5 wt% boron, and 0.9 wt%. Represents "Ni-17.0Cr-4.0Fe-4.3Si-3.5B-0.9C", which is an alloy containing a large amount of carbon and the remaining nickel. "D" in the "Undercoat" column contains 10.0 wt% chromium, 2.0 wt% iron, 3.0 wt% silicon, 2.0 wt% boron and the balance nickel. It represents “Ni-10.0Cr-2.0Fe-3.0Si-2.0B” which is an alloy contained. “E” in the “Undercoat” column is 18.0% chromium, 12.0% tungsten, 2.0% iron, 2.0% molybdenum and 3.6% by weight. "Ni-18.0Cr-12.0W-2.0Fe-2.0Mo-3.6Si-3.3B-" is an alloy containing 3 wt% silicon, 3.3 wt% boron, 0.9 wt% carbon and the balance nickel. 0.9C ”. “F” in the “Undercoat” column is 13.0 wt% chromium, 4.0 wt% iron, 4.0 wt% silicon, 3.0 wt% boron, and 0.6 wt% Represents "Ni-13.0Cr-4.0Fe-4.0Si-3.0B-0.6C", which is an alloy containing the above carbon and the remaining nickel. “G” in the “undercoat layer” column represents a mixture of 35 wt% “WC / 12Co” and 65 wt% “Ni-14.0Cr-4.0Fe-4.3Si-3.5B-0.7C” “Ni-14.0Cr-4.0Fe-4.3Si-3.5B-0.7C” consists of 14.0 wt% chromium, 4.0 wt% iron, 4.3 wt% silicon and 3.5 wt% An alloy containing boron, 0.7 wt% carbon and the balance nickel. “H” in the “undercoat layer” column represents a mixture of 50 wt% “WC / 12Co” and 50 wt% “Ni-14.0Cr-4.0Fe-4.3Si-3.5B-0.7C”. “I” in the “undercoat layer” column represents “Ni-1.5B-0.1C” which is an alloy containing 1.5 wt% boron, 0.1 wt% carbon and the balance nickel. .

  The topcoat layer was formed by a high-speed flame spraying method using “JP-5000”, which is a high-speed flame sprayer manufactured by PRAXAIR / TAFA. The thermal spray material used at the time of forming the top coat layer and the thickness of the formed top coat layer are as shown in the “top coat layer” column of Tables 1 to 3. “W2011XJ” in the “Topcoat layer” column represents a mixture of 90 wt% “WC / 20CrC / 10Ni” and 10 wt% metallic nickel.

  As thermal spraying conditions when spraying “WC / 12Co” or “WC / 20CrC / 7Ni” to form a topcoat layer, the oxygen flow rate is 893 L / min, the kerosene flow rate is 0.32 L / min, and the spraying distance is 380 mm. The spraying material supply rate was set to 100 g / min, and the nozzle length of the sprayer was set to 8 inches (about 203 mm). The spraying conditions for spraying “WC / 10Co / 4Cr” to form the topcoat layer are as follows: oxygen flow rate is 870 L / min, kerosene flow rate is 0.38 L / min, spraying distance is 380 mm, and the spraying material feed rate is The nozzle length of the sprayer was set to 8 inches (about 203 mm). As thermal spraying conditions when spraying “W2011XJ” to form a topcoat layer, the oxygen flow rate is 682 L / min, the kerosene flow rate is 0.38 L / min, the spraying distance is 380 mm, the spraying material supply rate is 100 g / min, The nozzle length of the thermal sprayer was set to 4 inches (about 102 mm).

  In the “Shock Resistance” column of Tables 1 and 2, the results of four-stage evaluation of the impact resistance of the laminates obtained in Examples 1 to 26 and Comparative Examples 1 to 6 are shown. The impact resistance of the laminate was evaluated based on the results of a falling ball impact test. In the falling ball impact test, the operation of dropping and colliding 250 superhard spheres on each laminate was performed on the surface of the laminate (in the case of Examples 1 to 26 and Comparative Examples 1 and 4 to 6, the topcoat layer and Comparative Example 2). In the case of, 3, the process was repeated until cracks or peeling occurred in the undercoat layer. The super hard sphere was dropped through the guide pipe from a height of 1 m at an angle of 60 degrees with respect to the laminate. Each superhard sphere has a diameter of 10 mm and a weight of 6 g.

  "◎" in the "Shock resistance" column indicates that when the laminate is subjected to a falling ball impact test, the number of operations (the number of times of use) repeated until the surface of the laminate is cracked or peeled is 200 times. This means that the impact resistance is excellent. “◯” in the “Shock Resistance” column indicates that the surface of the laminate is cracked or peeled by an operation of 100 times or more and less than 200 times, and means that the impact resistance is good. “Δ” in the “Shock resistance” column indicates that the operation of 50 times or more and less than 100 times indicates that the surface of the laminate is cracked or peeled off, and means that the impact resistance is moderate. "X" in the "Shock resistance" column represents that the surface of the laminate is cracked or peeled by an operation less than 50 times, and means that the impact resistance is poor.

  As shown in Tables 1 and 2, the laminates of Examples 1 to 26 each had an impact peel resistance evaluation of ◎ to Δ. In contrast, the laminates of Comparative Examples 4 and 5 that did not have an undercoat layer had an impact resistance peel evaluation of x.

  In the "Abrasion resistance" column of Tables 1 and 2, the results of four-stage evaluation of the abrasion resistance of the laminates obtained in Examples 1 to 26 and Comparative Examples 1 to 6 are shown. Evaluation of the abrasion resistance of the laminate was performed based on the result of a wear test in accordance with JIS H 8682-1. In the abrasion test, the surface of the laminate was rubbed with a load of 3.15 kgf (≈31 N) using abrasive paper CP180 (US CAMI standard) using a Suga abrasion tester.

  “◎” in the “Abrasion resistance” column indicates that the wear volume of the laminate when the laminate is subjected to the wear test is divided by the wear volume of the SS400 steel plate when the SS400 steel plate is subjected to the same wear test. Represents a value of less than 0.05, meaning that the wear resistance is excellent. “O” in the “Abrasion resistance” column indicates that the ratio of the wear volume of the laminate to the wear volume of the SS400 steel sheet is 0.05 or more and less than 0.1, which means that the wear resistance is good. To do. “X” in the “Abrasion resistance” column indicates that the ratio of the wear volume of the laminate to the wear volume of the SS400 steel sheet is 0.1 or more, which means that the wear resistance is poor.

  As shown in Tables 1 and 2, the laminates of Examples 1 to 26 and Comparative Examples 1 and 4 to 6 all had an evaluation of wear resistance. This result suggests that the abrasion resistance of the laminate is not greatly affected by the presence or absence of the undercoat layer.

  The “impact peel resistance improvement” column of Table 3 shows the results of four-stage evaluation of the impact peel resistance improvement of the laminates obtained in Examples 27 to 33 and Comparative Example 7. The evaluation of the improvement in impact peel resistance was performed based on the results of a falling ball impact test.

  “◎” in the “impact resistance improvement” column indicates the number of times that the laminate was subjected to a ball drop impact test, and the topcoat layer was formed directly on the substrate without forming the undercoat layer. The value obtained by dividing the laminate produced by the formation by the number of service life when subjected to the same falling ball impact test is 2.0 or more, and the impact peel resistance is greatly improved. Means. “O” in the “Improvement of impact resistance” column indicates that the ratio of the number of times of durability of the laminate with the undercoat layer to the number of times of durability of the laminate without the undercoat layer is 1.5 or more and less than 2.0. This means that the impact peel resistance is improved first of all. "△" in the column "Improvement of impact resistance" indicates that the ratio of the number of times of durability of the laminate with the undercoat layer to the number of times of durability of the laminate without the undercoat layer is 1.0 or more and less than 1.5. This means that the impact peel resistance is slightly improved. “X” in the column “Improvement of impact resistance” indicates that the ratio of the number of times of durability of the laminate with the undercoat layer to the number of times of durability of the laminate without the undercoat layer is less than 1.0. This means that the impact resistance is not improved.

As shown in Table 3, the laminates of Examples 27 to 33 all had an evaluation of the degree of improvement in impact peel resistance of ◎ to Δ.
Next, the technical idea that can be grasped from the embodiment will be described below.

The method for forming a thermal sprayed coating according to claim 4 or 5, wherein the formation of the first coating is performed by an overlay welding method or a flame spraying method.
-The laminated body as described in any one of Claims 1-3 whose porosity of a said 1st membrane | film | coat is 10% or less.

-The laminated body according to any one of claims 1 to 3, wherein the thickness of the first coating is 0.1 mm or more and 5 mm or less.
The laminate according to claim 1 or 2, wherein the second coating is a thermal spray coating formed by thermal spraying of a thermal spray material made of cermet powder or a mixed powder of cermet and metal.

The method of forming a thermal spray coating according to claim 4 or 5, wherein the second coating is formed by thermal spraying of a thermal spray material made of cermet powder or a mixed powder of cermet and metal.
-The laminated body of Claim 3 whose quantity of the tungsten carbide in the said thermal spray material is 50 weight% or more.

  The thermal spray coating according to claim 4 or 5, further comprising a step of heating the first coating formed on the base material to a semi-molten state prior to the formation of the second coating. Forming method.

The method for forming a sprayed coating according to claim 4 or 5, wherein the second coating is formed by any one of a high-speed flame spraying method, an explosion spraying method, and a cold spray method.
The method of forming a thermal spray coating according to claim 4 or 5, wherein the formation of the second coating is performed by a thermal spraying method in which a spray speed of the thermal spray particles is greater than 400 m / sec.

  -The laminated body according to any one of claims 1 to 3, wherein the thickness of the second film is 50 µm or more and 800 µm or less.

Claims (5)

A substrate having a Vickers hardness of 500 or less,
A first coating provided on the substrate;
A laminate comprising a thermal spray coating as a second coating provided on the first coating,
The laminate according to claim 1, wherein the first film has a Vickers hardness higher than that of the base material and lower than 810. A substrate having a Vickers hardness of 600 or more;
A first coating provided on the substrate;
A laminate comprising a thermal spray coating as a second coating provided on the first coating,
The laminate according to claim 1, wherein the first film has a Vickers hardness lower than that of the base material and higher than 230.   3. The laminate according to claim 1, wherein the second coating is a sprayed coating formed by spraying a cermet powder or a sprayed material made of a mixed powder of cermet and metal, and the sprayed material contains tungsten carbide. body. Forming a first film on a substrate having a Vickers hardness of 500 or less;
Forming a thermal spray coating as a second coating on the first coating formed on the substrate, comprising:
The method for forming a sprayed coating, wherein the first coating has a Vickers hardness higher than that of the substrate and lower than 810. Forming a first film on a substrate having a Vickers hardness of 600 or more;
Forming a thermal spray coating as a second coating on the first coating formed on the substrate, comprising:
The method for forming a sprayed coating, wherein the first coating has a Vickers hardness lower than that of the substrate and higher than 230.