WO2004076709A1 - 鉄系部品およびその製造方法 - Google Patents
鉄系部品およびその製造方法 Download PDFInfo
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- WO2004076709A1 WO2004076709A1 PCT/JP2004/002412 JP2004002412W WO2004076709A1 WO 2004076709 A1 WO2004076709 A1 WO 2004076709A1 JP 2004002412 W JP2004002412 W JP 2004002412W WO 2004076709 A1 WO2004076709 A1 WO 2004076709A1
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- Prior art keywords
- iron
- nickel
- carbon
- base material
- layer
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Classifications
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C12/00—Solid state diffusion of at least one non-metal element other than silicon and at least one metal element or silicon into metallic material surfaces
- C23C12/02—Diffusion in one step
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/06—Surface hardening
Definitions
- the present invention relates to iron-based parts used as various mechanical elements and mechanical parts made of iron or iron-based alloys and a method for producing the same, and in particular, in addition to sliding conformity and corrosion resistance of iron-based parts
- the present invention relates to a surface modification technique in which the height is suitably adjusted.
- compositions can be selected to those containing other elements such as carbon, and it can be manufactured from materials made from molten metal (hereinafter referred to as “meltable materials”), and metal powders and other additive powders.
- molten metal hereinafter referred to as “meltable materials”
- metal powders and other additive powders hereinafter referred to as “sintered material”
- sintered material can also be formed and sintered.
- a mold When manufacturing the above-mentioned machine elements and the like from a molten material, while being formed into a target shape by various processing means such as plastic working, shearing, and cutting, while manufacturing from a sintered material, a mold It is molded into a shape close to the target shape by powder molding.
- modification treatments such as carburizing, nitriding, quenching and tempering, and plating are performed depending on the required properties.
- structural carbon steel Nickel plating may be applied to surfaces with relatively poor corrosion resistance such as.
- the surface of the metallized member to be covered with the metallized member is such as smoothening the change in hardness from alloy steel to nickel metallized.
- nickel plating is easily peeled off from the alloy steel because no special treatment is applied to the change in hardness toward the deep part of the steel.
- the hardness from the plating surface to the inside of the plating member is suitably adjusted in the depth direction, thereby peeling the plating from the plating member.
- the present invention has been made in view of the above-mentioned requirements, and in addition to excellent sliding resistance and corrosion resistance, in particular, an iron-based steel having a suitably adjusted hardness from the surface of the plating to the inside of the coated member.
- the purpose is to provide parts.
- the surface of iron or iron-based alloy is coated with a carbon-containing nickel layer or a carbon-phosphorus-containing nickel layer, and the iron or iron-based alloy base is In addition to the formation of a nickel diffusion layer of decreasing amount, at least the surface layer of this nickel diffusion layer is characterized by containing carbon.
- the iron-based component of the present invention is coated with a Nigel layer on the surface of iron or iron-based alloy (hereinafter referred to as "base material"), the requirements of the techniques described in the above-mentioned patent documents are required. It is possible to realize the characteristics, that is, excellent sliding conformity and corrosion resistance. As a premise of realizing such a required characteristic, the iron-based component of the present invention is, Since the nickel diffusion layer in which the Nigel layer decreases toward the metal layer is formed, and the nickel layer and the base material are diffusion bonded, peeling of the nickel layer from the base material can be prevented. In addition, since the iron-based component of the present invention does not contain carbon or carbon and phosphorus in the above-mentioned nickel layer, the hardness and strength of the nickel layer can be sufficiently enhanced, and It has both dynamic compatibility and wear resistance.
- the nickel diffusion layer can be a hardened metal structure including martensite.
- the surface of the base material is coated with a nickel layer, it is desirable that the above-mentioned iron-based parts be applied to mechanical elements or mechanical parts that are required to be particularly resistant to wear or corrosion.
- the above-mentioned iron-based parts can be manufactured using a base material obtained from a sintered material, as well as using a base material obtained from a molten material.
- Phosphorus contained in the electroless nickel plating film increases the hardness of the nickel layer.
- phosphorus in the electroless nickel plating film has a carburizing property to the base material, a carburizing property to the Nigel layer from the base material and a function to suppress the permeation of carbon, and the phosphorus content of the electroless nickel plating film
- the carbon content of the heat-treated base material can be adjusted.
- the present invention is a method for suitably producing the above-described iron-based component, wherein a nickel layer is formed on the surface of an iron base material or a carbon-containing iron base alloy base material.
- the carbon content of the iron-based alloy is in the carburizing gas atmosphere
- the carbon content of the iron-based alloy is in the carburizing gas atmosphere in the range of 0.1 to 1.2%. It is characterized in that it is heated after heating to the austenite region temperature in the iron-carbon standard phase diagram and then cooled either in the gas atmosphere of the equilibrium carbon potential or in the gas atmosphere of the carbon potential lower than the carbon content of the base material. .
- the above-mentioned embodiment can realize excellent sliding conformability and corrosion resistance of the iron-based component. Can prevent the exfoliation of the nickel layer from the base material, and provide the Nikkol layer with excellent sliding conformability, wear resistance and corrosion resistance, and also increase the hardness and strength of the etch diffusion layer be able to.
- a nickel layer is coated on the surface of an iron base material or an iron-based alloy base material, and after heating to an austenite region temperature in an iron-carbon standard phase diagram, quenching and tempering It is characterized by giving.
- the base material By hardening and tempering, the base material can be hardened, the structure and mechanical properties can be stabilized, and the toughness can be recovered and the residual stress can be reduced.
- carburizing and quenching may be mentioned.
- the heating at the tenite zone temperature is maintained at a first temperature at which carburization and diffusion of nickel are promoted, and then maintained at a second temperature lower than the first temperature for hardening. It is desirable to apply That is, after promoting carburization at a temperature (about the above first temperature) about 100 ° C. higher than the A 3 transformation point of the iron-based material, a temperature about 50 ° C. higher than the A 3 transformation point ( By holding and diffusing at the above second temperature) and performing quenching, it is possible to obtain a part having a relatively large amount of carburizing and less generation of residual cast iron due to quenching. '
- the nickel layer can be laminated by an electric nickel plating, an electroless nickel plating, or both of them.
- the nickel layer is a nickel ⁇ phosphorus plating film having a phosphorus content of 15% by mass or less formed by electroless nickel plating
- the above phosphorus is contained when the carburizing amount to the iron or iron-based alloy is increased.
- the phosphorus content in the nickel plating film by electroless nickel plating can be adjusted by the sodium hypophosphite content in the plating solution and the PH (hydrogen ion concentration).
- Ni 3 P trinickel monophosphate
- the phosphorus content in the nickel layer suppresses the carburizing property by causing the appearance of the above-mentioned eutectic.
- the carburizing adjustment to the base material can be performed by adjusting the phosphorus content in addition to the carbon potential and the heating temperature in the gas atmosphere.
- the phosphorus content in the nickel layer suppresses the carburizing property to the nickel layer, so that electroless
- the carbon content of the heat-treated base material can be adjusted by adjusting the phosphorus content in the nickel plating layer.
- the iron-based parts used in the method of manufacturing iron-based parts as described above can of course be manufactured using a base material obtained from a molten material, and it is needless to say that the base material obtained from a sintered material is used. It can be manufactured using.
- a nickel plating layer is formed on the surface of the base material and heated at an austenitic region temperature, and carbon in the gas atmosphere or carbon in the base material between the base material and the nickel layer.
- the surface of the base material can be covered with a Niggels layer containing carbon by slow cooling or quenching, and the Nikkels layer can be firmly bonded to the iron base. . Therefore, in the present invention, regardless of carbon-free iron to carbon-containing iron-based alloys, even with relatively low-grade iron-based materials, it is possible to provide corrosion resistance to the surface and to slide with excellent counterparts. It is promising in that it can provide machine elements and components that have conformability and that the surface layer is hard and the inside is rich in toughness.
- FIG. 1 is a graph showing the depth from the surface of the heat treated nickel plated nickel body (Example 1) and the concentration of each element.
- FIG. 2 is a graph showing the depth from the surface of the heat treated nickel plated nickel (Example 3) and the concentration of each element.
- FIG. 3 shows an appearance photograph after the salt spray test, in which A is a sample of Example 1 and B is a sample as it has been subjected to an electro nickel plating.
- Base material consisting of iron or iron base alloy
- the base material of iron or iron alloy to be coated either ingot material or sintered material can be used.
- the ingot material can be applied to low carbon steel with a low carbon content and various alloys, such as carbon steel for machine structural use.
- the base material of the molten material is formed by a usual method such as plastic working, punching, cutting, and grinding, and can be subjected to post-treatments such as barrel polishing and shot blast if necessary.
- sintered materials are used in pure iron, alloy systems such as Fe-C u and F e-C u-C systems which do not contain additive elements, and N which has high mechanical strength. Sintered alloys containing elements such as i, Cr, Mo and V can be used.
- the density can be about 6.5 M g / m 3, but one having a high density and few pores is preferable because it is difficult for a plating solution to enter the pores.
- the sintered body can be subjected to post processing such as cutting, barrel polishing and shot blasting.
- the plating step is generally realized by sequentially performing an alkaline immersion degreasing treatment, an electrolytic cleaning treatment, an acid activation treatment, a base nickel plating treatment, and a nickel plating treatment on a base material composed of iron or iron alloy.
- the treatment liquid and treatment time of each process are as follows.
- the alkaline immersion degreasing treatment is performed by immersion in a warm solution of an aqueous solution containing sodium hydroxide, sodium cayrate, sodium phosphate, sodium carbonate for about 10 minutes.
- the electrolytic cleaning treatment is performed by immersing for about 10 minutes in a warm solution of an aqueous solution containing sodium hydroxide, sodium cayate and sodium carbonate by applying a current of 10 A / dm 2 in current density.
- acid activation treatment is performed by immersing in an aqueous solution of hydrochloric acid for about 1 minute.
- base nickel plating is performed by immersion in an aqueous solution containing nickel chloride and hydrochloric acid at a current density of 5 to 10 AZ dm 2 for about 15 minutes.
- nickel plating is performed by immersion in an aqueous solution containing nickel sulfate, nickel chloride and boric acid for about 12 minutes with a current density of 5 AZ dm 2 applied.
- Electroless nickel plating is according to the prior art.
- the plating process is generally realized by sequentially performing an alkaline immersion degreasing process, an acid activation process, and an electroless nickel plating process on a base material composed of iron or an iron alloy.
- the treatment solution and treatment time for each process are as follows.
- the alkaline immersion degreasing treatment is performed by immersion in a warm solution of an aqueous solution containing sodium hydroxide, sodium cayrate, sodium phosphate, sodium carbonate for about 10 minutes.
- acid activation treatment is performed by immersing in a hydrochloric acid aqueous solution for about 1 minute.
- electroless nickel plating is sodium hypophosphite, sodium citrate, sodium acetate and salts. Soak in warm solution of aqueous solution containing nickel fluoride for about 25 minutes.
- this electroless nickel plating can be made into nickel and phosphorus, and in this case, the phosphorus content can be adjusted by the content and pH of sodium hypophosphite in the plating solution.
- the thickness of the nickel plating layer can be appropriately set depending on the dimensional accuracy of the product, corrosion resistance, etc. However, the thickness is usually about 2 to 8 m.
- the thickness of the nickel plating layer can be controlled by the immersion time in the plating solution.
- the nickel plating layer can be formed by laminating at least one of an electric nickel plating and an electroless nickel plating to form a multilayer nickel plating layer.
- the heat treatment may be performed either in the form of slow cooling after heating to the temperature of the austenite region of the iron-based material, or in the form of quenching or tempering.
- the former is effective when obtaining a soft part in expectation of the nickel diffusion effect to the base material, and the latter is suitable when obtaining a harder part in expectation of the above effect.
- the heat treatment gas atmosphere is heated in a carburizing gas atmosphere for a base material containing no carbon.
- the carbon potential of the carburizing gas atmosphere is determined according to the carbon content of the base material. For example, in the case of an iron alloy having a carbon content of about 0.2% by mass, the bond potential is about 0.6% to about 0.8%.
- the heat treatment temperature is set to A 3 transformation point or more to about 8 5 0 to 9 0 0 ° C
- heating time is set to about 9 0-1 8 0 min.
- the temperature range to be carburized is a relatively high temperature, for example, a temperature about 100 ° C. higher than the A 3 transformation point.
- the holding temperature may be around A 3 transformation temperature, for example A 3 approximately 5 0 ° C than the transformation point higher temperatures.
- Tempering is carried out by heating at a temperature of around 180 ° C for about 1 hour, and letting it cool, according to the normal operation. It is possible to carry out the heat treatment gas atmosphere with the same carbon potential as the amount of carbon of the base material with respect to a base material containing carbon. According to the heat treatment in a gas atmosphere with such an equilibrium carbon concentration, carburization is performed from the gas atmosphere and the base material into the nickel film, and the carbon content of the nickel layer and the iron-based material becomes almost the same. Diffuse to the base material.
- the base material to be employed preferably has a carbon content of about 0.4 to 0.6% by mass.
- the heat treatment of the base material having a relatively high carbon content can be performed in a gas atmosphere of a carbon potential smaller than the carbon content of the base material, and in this case, for example, about 0.4 to 0.9% by mass of carbon amount A base material can be applied.
- carbon in the gas atmosphere and the base material carburizes the nickel layer.
- the amount of carbon decreases and Nigel diffuses.
- the heat treatment gas atmosphere does not have carbon potential, carburization to the nickel film is performed only from the base material, and the carbon amount of the base material decreases and the carbon amount on the nickel film surface becomes low.
- the carbon potential of is preferably 0.1% or more.
- a nickel-plated base material is heated in a carburizing gas and annealed to cover the surface with a nickel layer, and the lower layer of the nickel layer becomes iron pearlite structure or mixed structure of ferrite and pearlite. If the base material before heat treatment does not contain carbon and the volume is large, the core of the base material may have a ferrite structure. If the base material before heat treatment contains carbon, the gradually cooled product will have an iron perlite structure or a mixed structure of ferrite and perlite. Also, using a base material made of sintered material The surface is sealed by the nickel layer.
- the hardenability is improved in the region containing carbon and in which nickel and iron are diffused.
- the surface layer portion of the base material is in a state where it tends to be a martensitic structure by rapid cooling. Since the nickel content of the base material decreases from the surface layer of the base material toward the deep part, even if the surface part of the base material has a martensitic structure, the deep part may become a trousseite structure or a bainite structure. is there.
- the core of the base material has a ferrite structure.
- Products obtained by heating and annealing a nickel-plated carbon-containing base material in a gas of the same carbon potential as the carbon content of the base material form a pearlite structure or a mixed structure of ferrite and pearlite.
- Products made by heating and annealing using a carbon-containing base material in a gas atmosphere of carbon potential lower than that of the base material also become a pearlite structure or a mixed structure of ferrite and pearlite.
- the area where nickel spreads to the iron base has improved hardenability, so if the cooling rate is relatively fast, it will have a peony structure or a fine perlite structure.
- the concentrations of carbon, nickel, phosphorus and iron shall be analyzed by Mi croanalyzer).
- the cross-section of a nickel-plated base material heated in carburizing gas and annealed is analyzed by EPMA, and the concentration of each element is generally as follows. That is, the carbon concentration is highest at the surface of the nickel layer and decreases toward the inside. The nickel concentration is low on the surface of the nickel layer because the surface of the nickel layer contains a large amount of carbon.
- the nickel concentration shows the maximum value slightly deeper from the surface of the nickel layer, and the nickel concentration decreases due to the diffusion to the iron base toward the deeper part. .
- the phosphorus concentration is similar to the nickel concentration pattern, is low at the surface of the nickel layer, shows a maximum value when the carbon concentration decreases slightly toward the deep part, and the iron and nickel in the deep part diffuse to each other. Decline towards. Note that the higher the phosphorus content in the nickel film, the lower the carbon concentration and the smaller the carbon diffusion depth from the surface. In contrast, the iron concentration decreases towards the surface of the product by the diffusion of nickel, carbon or phosphorus.
- the heat-treated nickel layer surface exhibits a dull white-gray color.
- soot may adhere to the surface of the nickel layer, but this can be removed by barrel polishing or the like.
- the Nikkol layer is free from defects such as pits by heat treatment and is in a state of being metallurgically bonded to the base metal, and in the case of a sintered material with pores in particular, the surface is sealed, so it has excellent corrosion resistance. It becomes a thing.
- a salt spray test of the as-nickel-clad product and the heat-treated product shows a clear difference.
- Atomized iron powder (Atomel 3 0 0 M: made by Kobe Steel, Ltd.), electrolytic copper powder (CE 1 5: made by Fukuda metal foil powder industry), graphite powder (made by Southwestern) and lubricant (zinc stearate) are specified.
- the mixed powder was compression molded in a mold and sintered at a temperature of 1 12 CTC in butane modified gas.
- the composition of the sintered body was 1.5 mass% of copper, the bound carbon content was 0.2 mass%, and the density was 6.7 M g Zm 3 .
- a sintered body to which electric nickel plating was applied (Example 1) and a sintered body to which electroless nickel plating was applied (Example 2) were manufactured.
- the thickness of the muck was 5 m here.
- the phosphorus content in the electroless nickel plating was low.
- quenching and tempering were sequentially applied to each sample. Quenching is After heating at a temperature of 800 ° C. for 2 hours in a carburizing gas atmosphere with a carbon potential of 0.8%, oil quenching was performed. In addition, tempering was performed by heating in the atmosphere at a temperature of 180 ° C. for 1 hour and gradual cooling.
- the base material was manufactured by the same raw material powder and manufacturing method as in Examples 1 and 2 described above, except that the bonded carbon content of the sintered body was 0.6% by mass.
- the sintered body was manufactured into an electric nickel plated (Example 3) and an electroless nickel plated (Example 4), each in a gas atmosphere with a carbon potential of 0.1%. After heating at a temperature of 80.degree. C. for 1 hour, the oil was quenched and tempered.
- the base material is manufactured by the same method as in the above-mentioned Examples 3 and 4, and the sintered carbon has an amount of bonded carbon of 0.6% by mass.
- the sintered body was subjected to electric nickel plating in the same manner as in the above example, and then heated for 2 hours at a temperature of 80.degree. C. in a gas atmosphere of carbon potential 0.6% to carry out quenching and tempering. Was produced.
- Example 1 and Example 2 the surface layer portion of the base material has a structure including martensite. This is because nickel diffuses into the base material and is carburized.
- the hardness of electrolessly plated products is slightly lower than that of electrically plated products in both the surface and deep sections. This is because the phosphorus of the electroless nickel plating film suppresses carburization.
- Example 3 and Example 4 the hardness of the surface layer of the base material is low. This is because the carbon content of the base material decreased during heating because the carbon potential of the atmosphere gas for heat treatment was low.
- electroless nickel plating as compared to electro nickel plating (Example 3) The hardness of Example 4 is slightly high.
- the surface layer of the base material has a structure including martensite. This is because nickel diffuses into the base material and the carbon content of the base material made of an iron-based sintered alloy is high.
- FIG. 1 the cross section of the heat-treated body of Example 1 (a heat treatment in a gas atmosphere of 0.2% C base material, electric plating, carbon potential 0.8%) is shown in FIG. 1. .
- the vertical axis shows the concentration (detection count) of each element, and the horizontal axis shows the depth from the surface.
- the cross section of the heat-treated body of Example 3 (a heat treatment in a gas atmosphere of 0.6% C base material, electric plating, carbon potential 0.1%) was line analyzed by EPMA, It is shown in the figure. According to FIG.
- Example 2 a heat treatment in a gas atmosphere of 0.2% C base material, electroless plating, carbon potential 0.8%) is not shown, but both iron, nickel and carbon A pattern similar to the pattern shown in FIG.
- the difference from the case of Fig. 1 is that carbon is slightly less on the surface and carburization depth is also slightly less. This is because phosphorus suppresses carburization.
- the surface was small, and the maximum value was shown at about 4 im from the surface.
- phosphorus decreased toward the deeper part and was diffused from the surface to about ⁇ .
- the heat treatment body of Example 4 heat treatment in a gas atmosphere of 0.6% C base material, electroless plating, 0.1% carbon potential
- iron and nickel are not shown. Both carbon and carbon showed the same pattern as shown in Fig.2. In this case, phosphorus was found to diffuse about 5 m in the base material.
- the heat treatment body of Example 5 a heat treatment in a gas atmosphere of 0.6% C base material, electric plating, carbon potential of 0.6%) is not shown, but both of iron, nickel and carbon A pattern similar to the pattern shown in the figure is shown. Different The point is that the carbon concentration on the surface of the nickel layer and that of the base material are almost the same. This is because the carburization to the nickel layer was supplied from the gas atmosphere of the heat treatment and the carbon contained in the base material. There is little diffusion of nickel into the base material.
- FIG. 3 is a sample appearance photograph after the salt spray test has been performed for 96 hours.
- A is a sample of Example 1
- B is a sample not subjected to heat treatment as electroplated with nickel.
- the as-electroplated nickel sample a large amount of brown wrinkles is generated, and although it is covered with a nickel plating layer, it is considered that there are fine gaps.
- the occurrence of wrinkles was small in Examples 2 to 5 as in the sample of Example 1, and no difference was observed. This means that regardless of the gas atmosphere at the time of heat treatment, the nickel plating layer diffuses to the base material by heating and adheres securely, and defects such as fine cracks and pin poles of the nickel plating layer are repaired. Conceivable.
- Electroless nickel plating is applied to a machined base material made of carbon steel for mechanical structure with a carbon content of 0.5% by mass, and heated at a temperature of 80 ° C. for 90 minutes in a carburizing gas atmosphere. Quenched and tempered at a temperature of 180 ° C. for 1 hour. Electroless nickel plating was classified into three types: those with low concentration of phosphorus content in the nickel plating layer (Example 6), those with medium concentration (Example 7) and those with high concentration (Example 8). In each case, the thickness was 7 m.
- Example 6 in which the cross-sectional structure was low in phosphorus content, the deep portion was approximately 30 in the martensite, and the central portion was a finely divided pearlite structure transformed by heat treatment. This is because the diffusion of nickel into the iron base of the base material improves the hardenability of that portion. Furthermore, in Example 8 in which the phosphorus content is high, almost no martensitic structure is observed, and the pearlite and ferrite which are refined are Showed a mixed structure of This is because the diffusion of nickel is small and carburization is slight.
- the cross-sectional hardness of each heat-treated body is shown in Table 2 for these example 68. '
- Example 6 having a low phosphorus content is hard, and in Example 8 having a high phosphorus content, the hardness of the portion close to the surface is particularly low.
- the corrosion resistance of the above-mentioned Examples 6 to 8 according to the salt spray test was good as in the case of the sample shown in FIG. 3A of Example 1.
- the one with a low phosphorus content in the nickel plating layer (Example 6) has a large nickel diffusion depth and a carburized depth, and is reformed to be relatively thick. It turned out to happen. For this reason, those having a low phosphorus content are particularly suitable for parts to be quenched.
- the phosphorus content in the nickel plating layer is high (Example 8)
- the thickness of the nickel diffusion layer is 10 x m, and both carburizing and nickel are not carried out. It was found that the layer reached to the nickel diffusion layer. For this reason, it can be said that the bonding of the nickel layer is sufficiently performed, the corrosion resistance is high, and the nickel layer has a relatively hard property.
- the phosphorus content in the nickel plating layer suppresses the carburization and the diffusion of nickel
- the phosphorus content of the electroless nickel plating can be used as one of the means for controlling the carburizing amount and the diffusion of nickel.
- a product heat-treated in a gas atmosphere having a carbon potential can be obtained by The nickel of the nickel layer diffuses with the iron base, the mechanical strength is high, and high adhesion between the nickel layer and the base material is formed, making it difficult to peel off. Further, by heat treatment, the nickel layer is carburized by the gas atmosphere of heat treatment or carbon contained in the base material to become a Ni--C alloy, thereby becoming a softer phase slightly harder than nickel and eliminating defects in the plating layer.
- the Fe-Ni-C alloy part When hardened, the Fe-Ni-C alloy part becomes hard because it easily forms a martensitic structure, and if a base material with low carbon content or no carbon is used, the surface layer part becomes hard and the center
- the part can be a soft iron-based part.
- the heat-treated product when shot-burned or barrel-polished, it can be made to have a surface gloss.
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Abstract
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JP4789141B2 (ja) * | 2005-06-10 | 2011-10-12 | 株式会社吉野ハード | 鉄系部品の製造方法 |
JP5243764B2 (ja) * | 2007-10-03 | 2013-07-24 | 金井 宏彰 | カテーテルチューブ成形用芯材およびその製造方法 |
CN102676978B (zh) * | 2011-03-18 | 2014-12-17 | 台耀科技股份有限公司 | 改善非奥氏体系不锈钢表面机械性质的方法 |
JP6198652B2 (ja) * | 2014-03-24 | 2017-09-20 | 大同メタル工業株式会社 | 摺動部材 |
JP6198653B2 (ja) * | 2014-03-24 | 2017-09-20 | 大同メタル工業株式会社 | 摺動部材 |
JP6466268B2 (ja) * | 2015-06-30 | 2019-02-06 | 大同メタル工業株式会社 | 摺動部材 |
JP6466245B2 (ja) * | 2015-05-14 | 2019-02-06 | 大同メタル工業株式会社 | 摺動部材 |
JP6466246B2 (ja) * | 2015-05-14 | 2019-02-06 | 大同メタル工業株式会社 | 摺動部材 |
CN105603476B (zh) * | 2016-01-20 | 2018-12-25 | 锦州韩华电装有限公司 | 电枢铁芯表面电镀镍工艺 |
CN108568395B (zh) * | 2018-04-19 | 2021-01-12 | 宁波沈鑫电子有限公司 | 一种替代压铸铝表面阳极效果的喷漆工艺 |
Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS4826634A (ja) * | 1971-08-11 | 1973-04-07 | ||
JPS596368A (ja) * | 1982-06-30 | 1984-01-13 | Nitsuchi:Kk | リンクチエ−ンの製造方法 |
JPS596367A (ja) * | 1982-06-30 | 1984-01-13 | Nitsuchi:Kk | リンクチエ−ンの製造方法 |
JPS61572A (ja) * | 1984-06-11 | 1986-01-06 | Honda Motor Co Ltd | 鋼の浸炭方法 |
JPH0544016A (ja) * | 1991-08-12 | 1993-02-23 | Toyota Motor Corp | 薄膜形成方法 |
-
2004
- 2004-01-15 JP JP2004008440A patent/JP4467042B2/ja not_active Expired - Fee Related
- 2004-02-26 TW TW093104871A patent/TWI296290B/zh not_active IP Right Cessation
- 2004-02-27 KR KR1020057015895A patent/KR101049679B1/ko not_active IP Right Cessation
- 2004-02-27 CN CN2004800113254A patent/CN1780930B/zh not_active Expired - Fee Related
- 2004-02-27 WO PCT/JP2004/002412 patent/WO2004076709A1/ja active Application Filing
Patent Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS4826634A (ja) * | 1971-08-11 | 1973-04-07 | ||
JPS596368A (ja) * | 1982-06-30 | 1984-01-13 | Nitsuchi:Kk | リンクチエ−ンの製造方法 |
JPS596367A (ja) * | 1982-06-30 | 1984-01-13 | Nitsuchi:Kk | リンクチエ−ンの製造方法 |
JPS61572A (ja) * | 1984-06-11 | 1986-01-06 | Honda Motor Co Ltd | 鋼の浸炭方法 |
JPH0544016A (ja) * | 1991-08-12 | 1993-02-23 | Toyota Motor Corp | 薄膜形成方法 |
Also Published As
Publication number | Publication date |
---|---|
TWI296290B (en) | 2008-05-01 |
CN1780930B (zh) | 2011-06-22 |
KR101049679B1 (ko) | 2011-07-14 |
JP2004277880A (ja) | 2004-10-07 |
CN1780930A (zh) | 2006-05-31 |
KR20050107462A (ko) | 2005-11-11 |
JP4467042B2 (ja) | 2010-05-26 |
TW200424364A (en) | 2004-11-16 |
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