US20060073065A1 - Iron based sintered body excellent in enveloped casting property in light metal alloy and method for producing the same - Google Patents
Iron based sintered body excellent in enveloped casting property in light metal alloy and method for producing the same Download PDFInfo
- Publication number
- US20060073065A1 US20060073065A1 US11/280,217 US28021705A US2006073065A1 US 20060073065 A1 US20060073065 A1 US 20060073065A1 US 28021705 A US28021705 A US 28021705A US 2006073065 A1 US2006073065 A1 US 2006073065A1
- Authority
- US
- United States
- Prior art keywords
- powder
- sintered body
- iron based
- less
- based sintered
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Abandoned
Links
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
- C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/24—After-treatment of workpieces or articles
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F7/00—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression
- B22F7/06—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression of composite workpieces or articles from parts, e.g. to form tipped tools
- B22F7/08—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression of composite workpieces or articles from parts, e.g. to form tipped tools with one or more parts not made from powder
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B15/00—Layered products comprising a layer of metal
- B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
- B32B15/012—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of an iron alloy or steel, another layer being formed of aluminium or an aluminium alloy
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0207—Using a mixture of prealloyed powders or a master alloy
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/12—Both compacting and sintering
- B22F3/16—Both compacting and sintering in successive or repeated steps
- B22F3/164—Partial deformation or calibration
- B22F2003/166—Surface calibration, blasting, burnishing, sizing, coining
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/24—After-treatment of workpieces or articles
- B22F2003/245—Making recesses, grooves etc on the surface by removing material
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
- F05C—INDEXING SCHEME RELATING TO MATERIALS, MATERIAL PROPERTIES OR MATERIAL CHARACTERISTICS FOR MACHINES, ENGINES OR PUMPS OTHER THAN NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES
- F05C2251/00—Material properties
- F05C2251/04—Thermal properties
- F05C2251/042—Expansivity
Definitions
- the invention relates to an iron based sintered body, particularly to an iron based sintered body excellent in enveloped casting property in a light metal alloy.
- the iron based sintered body is used as being enveloped in a light metal alloy member such as an aluminum alloy by casting.
- Automobile parts made of an aluminum alloy as a kind of light metal alloys are widely used for making the automobile parts lightweight and for enhancing heat-release ability thereof.
- the aluminum alloys are insufficient in material characteristics as automobile structural members including poor mechanical properties such as strength, wear resistance and rigidity as well as high thermal expansion coefficient as compared with usually used cast iron.
- different kind of materials are enveloped in the aluminum alloy member by casting such as, for example, gravity casting and die casting, or the aluminum alloy member is compounded with different kind of materials.
- JP-A No. 60-219436 proposes an engine block having a bearing member of an aluminum alloy housing cap which is formed by enveloping an iron based material by casting.
- the aluminum alloy housing cap is attached under a main body of an aluminum alloy cylinder block.
- the mechanical strength is enhanced to an extent not attainable by using only the aluminum alloy with a large improvement of rigidity, and a proper amount of the clearance change by a difference of the thermal expansion coefficient between the bearing and the crank shaft is maintained.
- JP-U Japanese Utility Model Application Laid-Open
- JP-U Japanese Utility Model Application Laid-Open
- No. 63-150115 proposes a crank shaft supporting member of an internal combustion engine made of a light metal alloy.
- the inside of a portion of the supporting member partitioned with a center lines of bolt holes for mounting on a cylinder block and a curved crank journal supporting surface is reinforced with reinforcing fibers.
- JP-A 2001-276961 describes an art for producing a composite member impregnated with an aluminum alloy by a casting method, wherein molten aluminum alloy is allowed to permeate into a porous metal premolded body containing 10 to 40% by weight of chromium in iron or iron based alloy with a given time lag after completing injection of molten aluminum.
- JP-B No. 2-30790 proposes a method for producing an aluminum alloy casting by applying an intermetallic compound forming treatment, wherein a porous metal body is placed in a mold, the porous metal body is enveloped in an aluminum alloy by casting by a high pressure solidification casting method, and a layer of a compound between aluminum and metal element of the porous metal body is formed by heating at 450 to 550° C.
- JP-B No. 2-30790 proposes a method for producing an aluminum alloy casting by applying an intermetallic compound forming treatment, wherein a porous metal body is placed in a mold, the porous metal body is enveloped in an aluminum alloy by casting by a high pressure solidification casting method, and a layer of a compound between aluminum and metal element of the porous metal body is formed by heating at 450 to 550° C.
- FIGS. 1A and 1B schematically show examples of the shape of the iron based sintered body used in the examples
- FIG. 2 schematically shows the structure in the vicinity of the bearing of the internal combustion engine used in the examples.
- JP-A 60-219436 involved a restriction in designing arising from a problem that it is difficult to join the iron based material and an aluminum alloy without leaving any gaps, in addition to the problems that selection of iron based materials is necessary for controlling the bearing to have a desired thermal expansion coefficient. It is also a problem that production cost is forced to rise due to a requirement that the iron based material and aluminum alloy having different hardness with each other should be simultaneously machined. Furthermore, the iron based material which is enveloped by casting should be machined with high precision for arranging the iron based material at a desired position in a casting mold with high precision, which lead to additional increase of the production cost. A complex process is required for surface treatment such as aluminum plating on the surface of the iron based material in order to join the iron based material and aluminum alloy without any gaps, which leads to a further increase of the production cost.
- porous metal molded body disclosed in JP-A No. 2001-276961
- the aluminum alloy it is required for the aluminum alloy to be impregnated deep into the porous metal molded body for compounding, in order to stably obtain and satisfactory characteristics.
- the porous metal molded body should be preheated at a high temperature.
- the production cost is also forced to be increased in the art disclosed in JP-B No. 2-30790, since a composite production process is necessary for an intermetallic compound forming treatment.
- An object of the present invention is to solve the problems in the conventional art described above, and to provide an iron based sintered body excellent in enveloped casting properties in the light metal alloy and a method for producing the same.
- the iron based sintered body as an object of the invention is low in price and has a higher strength than a light metal alloy such as an aluminum alloy while having good machinability.
- the iron based sintered body which is an object of the invention is able to have a high bonding strength with the light metal alloy and has a higher strength and a lower thermal expansion coefficient than the light metal alloy after being enveloped in the light metal alloy such as an aluminum alloy by casting.
- Another object of the invention is to simplify the production process of members using the iron based sintered body, and to provide an iron based sintered body that is responsible for reducing the material cost.
- the inventors have made intensive studies on various factors affecting on enveloped casting property in the light metal alloy such as the aluminum alloy.
- the inventors have found that the enveloped casting property in the light metal alloy of the iron based sintered body and the bonding strength between the iron based sintered body and the light metal alloy is remarkably improved by allowing the iron based sintered body to have a structure containing a free Cu phase dispersed in the matrix, and by adjusting the surface roughness of the iron based sintered body in a specified range by applying a shot blast treatment or further applying a steam treatment.
- the iron based sintered body of the present invention has a composition of the matrix comprising, in % by mass, 0.5 to 2.5% of C and 5 to 40% of Cu, or further containing 40% or less in total of the one or more elements selected from the group of consisting of 30% or less of Cr, 10% or less of Mo, 3% or less of Ni, 3% or less of Si, 2.5% or less of Mn, 5% or less of V, 5% or less of Ti, 3% or less of Nb and 5% or less of W and the balance being Fe and inevitable impurities.
- C is an element for enhancing the strength and hardness of the sintered body, and 0.5% or more of C is required for ensuring the strength and for forming a matrix having a pearlite structure excellent in machinability.
- coarse carbide is formed when the content of C exceeds 2.5% to result in a decrease of machinability. Accordingly, the content of C is restricted in the range of 0.5 to 2.5%.
- Cu enhances the strength of the iron based sintered body by solid solution in the matrix.
- Cu is precipitated as a free Cu phase in the matrix, and reacts with the light metal alloy when the iron based sintered body is enveloped in the light metal alloy by casting. Thereby, the bonding strength between the iron based sintered body and light metal alloy is increased. Substantially the precipitation of the free Cu phase is not observed when the Cu content is less than 5% to fail in obtaining a desired bond strength.
- the content of Cu exceeds 40%, on the other hand, mechanical properties such as strength is decreased. Accordingly, the content of Cu is restricted in the range of 5 to 40%, preferably in the range of 10 to 30%.
- Cr, Mo, Ni, Si, Mn, V, Ti, Nb and W are elements for enhancing the strength of the iron based sintered body, and at least one of them may be added, if necessary.
- Cr, Mo, Ni, Si, Mn, V, Ti, Nb and W are added, if necessary.
- sintering becomes difficult and the strength of the iron based sintered body is decreased.
- Cr, V and W exceeding the above contents are added, machinability is decreased as a result of coarsening of carbides.
- the content of silicone oxide increases by adding Si in an content exceeding the above content to result in a decrease of the melting point as well as deterioration of machinability.
- the balance except the components above is Fe and inevitable impurities in the composition of the matrix of the iron based sintered body of the present invention.
- the iron based sintered body of the invention has the composition as described above and further between of the porosity, the matrix structure and free Cu phases dispersed in the matrix. Free graphite phases may be dispersed in the matrix with a volume ratio of 2% or less.
- the matrix has a pearlite structure in the iron based sintered body of the present invention, since the pearlite structure of the matrix permits machinability of the sintered body to be improved.
- the matrix structure may be a sorbite or troostite structure instead of the pearlite structure from the view point of machinability.
- a bainite structure, a martensite structure and a mixed structure thereof may be also acceptable without any problems.
- the free Cu phase dispersed in the matrix preferably accounts for 5 to 30% in volume ratio.
- the volume ratio of the free Cu phase of as small as less than 5% results in a decrease of the bonding strength since a small amount of an intermetallic compound of Cu and the light metal alloy is formed.
- the bonding strength is rather decreased since the strength of the iron based sintered body is reduced to below the strength of the light metal alloy.
- Increasing the volume ratio of the free Cu phase dispersed in the matrix permits the intermetallic compound to be formed by a reaction of the molten light metal alloy with free Cu phase when the sintered body is enveloped in the light metal alloy by casting. According to this mechanism, many bonding points are formed and a high bonding strength may be obtained even if the molten light metal alloy does not impregnate deep into the iron based sintered body.
- the iron based sintered body contains many pores, they are preferably formed as isolated each other or partially connected pores.
- the “partially connected pores” as used herein refers to pores which are connected each other or one another, but are not connected with more pores.
- isolated pores or partially connected pores means that the value defined by [(the volume of fully connected pores)/(the total volume of pores) ⁇ 100 (%)] is 50 or less.
- the pores are considered to be continuous when the value defined above is larger than 50.
- the total volume of the pores may be determined by converting the density measured by the Archimedes method.
- the volume of the fully connected pores can be determined by allowing a wax to permeate into the sintered body by immersing the sintered body in a liquid wax for 60 minutes, and by calculating the changes of the weight before and after permeation.
- the isolated pores or partially connected pores can prevent the molten alloy from impregnating deep into the iron based sintered body when the sintered body is enveloped in the alloy by casting. Consequently, the characteristics of the iron based sintered body is less deteriorated by impregnation of the light metal alloy to enable the strength and thermal expansion coefficient inherent to the iron based sintered body to be maintained.
- the porosity of the iron based sintered body of the invention is preferably 5 to 35% by volume.
- a large molding pressure is required for press-molding when the porosity is less than 5% by volume. Accordingly, the process is economically disadvantageous since a large size molding machine is necessary while decreasing productivity.
- the porosity exceeds 35% by volume, on the other hand, the cast light metal alloy impregnates so deep into the iron based sintered body that characteristics of the iron based sintered body is deteriorated.
- the porosity is determined by measuring the density of the sintered body by the Archimedes method followed by converting into the volume % of the pores.
- Fine particles for improving machinability are preferably dispersed in the matrix having above mentioned composition of the iron based sintered body of the invention for improving the machinability.
- the dispersed fine particles for improving machinability are at least one element selected from the group consisting of MnS, CaF 2 , BN and enstatite. Particles of MnS, CaF 2 , BN and enstatite are able to improve machinability, and they may be added by selecting depending on the requirements.
- the cutting resistance is maintained low by uniformly dispersing the fine particles in the matrix for improving machinability, since chips during the cutting is divided into a size determined by the distance between these fine particles.
- the fine particles for improving machinability dispersed in the matrix preferably has a particle diameter of 150 ⁇ m or less.
- the boundary strength is decreased when the particle diameter of the fine particles for improving machinability exceeds 150 ⁇ m.
- the preferable diameter of fine particles for improving machinability is in the range of 5 to 100 ⁇ m.
- the content of the fine particles for improving machinability dispersed in the matrix of the porous metal sintered body is preferably 0.1 to 5% by mass relative to the whole quantity of the mixed powder, or to the total amount of the iron based powder, copper powder, alloy element powder, graphite powder and fine particles for improving machinability. No machinability improving effect is observed when a content of the fine particles for improving machinability is less than 0.1% by mass.
- the adhesive strength of the light metal alloy to the matrix as well as the adhesive strength at the boundary are decreased when the content exceeds 5% by mass. Accordingly, the content of the fine particles for improving machinability with a particle diameter of 150 ⁇ m or less is in the range of 0.1 to 5% by mass.
- the iron based sintered body of the invention has a surface roughness Rz of 10 to 100 ⁇ m.
- the surface area is not sufficiently increased when Rz is less than 10 ⁇ m to fail in obtaining sufficient adhesive property and bonding strength between the sintered body and light metal alloy.
- Rz surface roughness
- size accuracy becomes insufficient and the surface layer tends to generate cracks, then the adhesive property and bonding strength is decreased.
- the iron based sintered body of the invention has grooves on the end faces and/or side faces as shown in FIGS. 1A and 1B in addition to having a surface roughness as described above.
- Forming the grooves on the end faces and/or side faces permits the surface area to be increased while further improving the adhesive property and bonding strength between the molten light metal alloy and iron based sintered body.
- the grooves on the end faces and/or side faces are preferably formed at the stage of compressed molding, and/or in the machining process of the green compact or the sintered body. While the shape of the groove is not particularly restricted, it is preferably V-shape or arc shape. The number of the grooves may be appropriately selected depending on the thickness, shape and size of the sintered body as shown in FIGS. 1A and 1B .
- the iron based sintered body of the invention having the composition and structure as described above has an average thermal expansion coefficient of 13.5 ⁇ 10 ⁇ 6 /° C. or less from the room temperature to 200° C.
- the iron based sintered body may have an average thermal expansion coefficient of 15.0 ⁇ 10 ⁇ 6 /° C. or less even after the light metal alloy has impregnated into the partially connected pores of the iron based sintered body, provided that the original average thermal expansion coefficient of the iron based sintered body is 13.5 ⁇ 10 ⁇ 6 /° C. or less from room temperature to 200° C.
- the thermal expansion coefficient of the iron based sintered body of the invention comes close to the thermal expansion coefficient of an iron based crank shaft of an internal combustion engine, which is 9 ⁇ 10 ⁇ 6 to 12 ⁇ 10 ⁇ 6 /K. Accordingly, the thermal expansion of the bearing during operation of the internal combustion engine can be suppressed when the iron based sintered body is enveloped in the bearing of the internal combustion engine by casting. This is effective for properly maintaining the change of clearance between the bearing and crank shaft caused by a difference of the thermal expansion coefficients between them.
- An iron based powder, a copper powder, a graphite powder and a lubricant powder, optionally fine particle powder for improving machinability, are mixed to form a mixed powder.
- the mixed powder is filled in a mold to form a green compact by press-molding, or compression molding. And then, the green compact is sintered to form a sintered body.
- the iron based powder used is preferably a pure iron powder and/or a stainless steel powder.
- the stainless steel powder is preferably a ferritic stainless steel powder or a martensitic stainless steel powder.
- ferritic stainless steel examples include SUS 430, SUS 410L and SUS 434.
- a representative composition thereof preferably comprises, in % by mass, 0.12% or less of C, 1.0% or less of Si, 1.25% or less of Mn, 11 to 18% of Cr and 1.25% or less of Mo, and optionally at least one element selected from the group consisting of 3% or less of Ni, 5% or less of V, 5% or less of Ti, 3% or less of Nb and 5% or less of W, and the balance being Fe and inevitable impurities.
- Examples of the martensitic stainless steel are SUS 420, SUS 410 and SUS 416.
- a representative composition thereof preferably comprises, in % by mass, 0.4% or less of C, 1.0% or less of Si, 1.25% or less of Mn and 11.5 to 14% of Cr, and optionally at least one element selected from the group consisting of 3% or of Ni, 5% or less of V, 5% or less of Ti, 3% or less of Nb and 5% or less of W, and the balance being Fe and inevitable impurities.
- a pure copper powder is preferably used as the raw material of the copper powder.
- the copper powder is added so that the content of Cu in the mixed powder is 5 to 40% by mass relative to the total content of the iron based powder, alloy element powder, copper powder, graphite powder and fine particle powder for improving machinability. No precipitation of free Cu is observed when the copper content is less than 5% by mass in the mixed powder. On the other hand, mechanical properties such as strength are decreased when the copper content exceeds 40% by mass. Accordingly, the content of Cu in the mixed powder is adjusted in the range of 5 to 40% by mass, preferably in the range of 10 to 30%.
- the graphite powder is added as the alloy element for enhancing the strength of the iron based sintered body and for improving machinability by forming the matrix structure into the pearlite structure. To obtain these effects, graphite is added so that the content of C in the mixed powder becomes 0.5 to 2.5% by mass.
- the lubricant powder is added in the mixed powder for improving moldability in the compression molding process and for increasing the density of the green compact.
- Zinc stearate is preferable as the lubricant powder.
- the content of the lubricant powder in the mixed powder is preferably 0.5 to 5 parts by weight relative to 100 parts of the whole quantity of mixed powder.
- the whole quantity of the mixed powder is the total amount of the iron based powder, copper powder, alloy element powder, graphite powder and fine particle powder for improving machinability.
- the fine particle powder for improving machinability may be also added to the mixed powder in addition to the iron based powder, copper powder, graphite powder and lubricant powder in order to improve machinability.
- the fine particle powder for improving machinability is preferably at least one element selected from the group consisting of MnS, CaF 2 , BN and enstatite powders.
- the MnS, CaF 2 , BN and enstatite powders are able to improve machinability, and they are selectively added if necessary.
- the fine particles for improving machinability preferably has a particle diameter of 150 ⁇ m or less. The bondary strength decreases when the particle diameter of the fine particles powder for improving machinability exceeds 150 ⁇ m.
- the preferable diameter of the fine particles powder for improving machinability is in the range of 5 to 100 ⁇ m.
- the preferable content of the fine particle powder for improving machinability in the mixed powder is, if any, 0.1 to 5% by mass relative to the total amount of the iron based powder, copper powder, alloy element powder, graphite powder and fine particle powder for improving machinability.
- the machinability improving effect cannot be obtained when the content of the fine particle powder for improving machinability is less than 0.1% by mass, while the boundary strength is decreased when the content of the fine particle powder for improving machinability exceeds 5% by mass.
- At least one of the powders selected from the group consisting of the Cr powder, Mo powder, W powder, Fe—Cr powder, Fe—Mo powder and Fe—W powder are further blended in the mixed powder above, alone or in combination, as the alloy element powder so that the total content thereof is 40% or less relative to the total amount of the iron based powder, alloy element powder, copper powder, graphite powder and machinability improving powder, whereby the mixed powder contains, in % by mass, 40% or less in total of one or more element selected from the group consisting of 30% or less of Cr, 10% or less of Mo, 3% or less of Ni, 3% or less of Si, 2.5% or less of Mn, 5% or less of V, 5% or less of Ti, 3% or less of Nb and 5% or less of W.
- the Cr powder, Mo powder, W powder, Fe—Cr powder, Fe—Mo powder and Fe—W powder are blended for improving the strength and decreasing the thermal expansion coefficient of the sintered body so that the blending amount is 40% or less in total in the mixed powder.
- the alloy elements are unevenly distributed and the strength of the sintered body decreases when the blending amount of these powders exceeds 40%.
- V-mill is preferably used for economical reasons.
- the mixed powder is filled in a mold for press-molding or compression-molding to obtain a green compact having a desired shape.
- the press-molding conditions of the green compact is preferably adjusted so that the sintered body has an average thermal expansion coefficient of 13.5 ⁇ 10 ⁇ 6 /° C. or less from room temperature to 200° C. While the method for molding the mixed powder is not particularly restricted, a press-machine is preferably used.
- the shape of the mold is previously designed so that grooves are formed on side faces and/or end faces of the green compact.
- the green compact is sintered at 1100 to 1250° C. to form a sintered body.
- the sintering condition is preferably adjusted so that the sintered body has an average thermal expansion coefficient of 13.5 ⁇ 10 ⁇ 6 /° C. or less from room temperature to 200° C.
- a reducing atmosphere is preferable for accelerating the sintering process.
- the sintering condition is preferably adjusted so that partially liquid-phase sintering is performed in order to form a sintered body containing isolated or partially connected pores. This method permits the pores to be isolated or partially connected since the pores are plugged with the free Cu phase.
- the sintered body is subjected to a shot blast treatment to have a surface roughness Rz of 10 to 100 ⁇ m.
- the diameter of shot particles and blowing pressure are controlled for adjusting the surface roughness.
- the surface is cleaned by removing surface oxidation films and the free Cu phase dispersed in the matrix is exposed to the surface by applying the shot blast treatment. Consequently, wettability between the surface of the sintered body and molten light metal alloy is improved to enable the reaction between the surface and molten alloy to be enhanced.
- the adhesive property is improved since bonding is formed with no interface gaps between the light metal alloy and the sintered body.
- the boundary strength is also improved due to an additional anchor effect as a result of the improvement of the adhesive property.
- the pores exposed to the surface are crushed by applying the shot blast treatment to enable the molten light metal alloy to be prevented from permeating into the sintered body during the enveloped casting process. Accordingly, the characteristics of the sintered body itself may be maintained after enveloped casting. However, no shot blast treatment is required when the surface roughness of the sintered body satisfies the range described above after sintering.
- the steam treatment is preferably applied to the sintered body subsequent to the shot blast treatment.
- the steam treatment is applied at 550 to 650° C. for 30 to 90 minutes in a steam atmosphere.
- An iron oxide coating film is formed on the surface and exposure of free Cu on the surface because remarkable due to this steam treatment, which further accelerates the reaction between the sintered body and molten light metal alloy to enable the interface to be bonded without leaving any gaps, thus improving the adhesive property.
- the pores in the vicinity of the surface of the sintered body is plugged by this steam treatment to prevent a large quantity of the molten light metal alloy from permeating deep into the sintered body by casting, and the characteristics of the iron based sintered body is maintained after the enveloped casting.
- the iron based sintered body of the invention is mounted on a corresponding site in a casting mold for forming the bearing of the internal combustion engine, and a light metal alloy member is produced by a high pressure die-casting by injecting the molten light metal alloy, for example a molten aluminum alloy, into the casting mold.
- the light metal alloy member is processed into a final product by machining it into a prescribed size.
- the iron based sintered body produced by the method as described above is mounted on a corresponding site in a casting mold, and the light metal alloy member is produced by the high pressure die-casting by injecting the molten light metal alloy.
- Preheating at a temperature of as high as 500 to 550° C. that has been inevitable in the conventional iron based sintered body is no more required in the iron based sintered body according to the invention. Instead, preheating at room temperature or up to 200° C. is sufficient for the iron based sintered body of the invention.
- the molten light metal alloy can be injected with good circulation into the casting mold with the iron based sintered body of the invention without preheating or with preheating at a low temperature, so that good adhesive property and bonding strength between the molten light metal alloy and sintered body may be ensured. Consequently, the production process of the light metal alloy member enveloping the iron based sintered body by casting may be simplified and the manufacturing cost of the light metal alloy member may be decreased.
- a mixed powder was prepared by mixing with kneading a pure iron powder as an iron based powder, a pure copper powder as a copper powder, a graphite powder, a zinc stearate powder as a lubricant powder and a MnS powder as a fine particle powder for improving machinability was further added to the mixed powder.
- the blending ratio of each powder in the mixed powder is shown in Table 1.
- the mixed powder was filled in a mold and was press-molded into a green compact having a shape as shown in FIG. 1A . Grooves being a depth of 0.5 mm were formed on end faces and side faces of a part of the green compact as shown in FIG. 1A .
- a green compact having a shape according to JIS Z2550 was formed as a tensile strength test piece.
- a green compact with a dimension of 50 mm in diameter and 15 mm in length was also prepared as a test piece for measuring a bonding strength after enveloped casting.
- a sintered body was produced by liquid-phase-sintering each of the green compact under an appropriate condition depending on the content of Cu.
- the sintered body obtained was further subjected to a shot blast treatment and additional steam treatment, if necessary.
- the shot blast treatment was carried out using a steel grid prescribed in JIS G70 at a blowing pressure of 0.049 MPa (5 kgf/cm 2 ).
- the steam treatment was carried out at 550° C. for 90 minutes.
- composition, content of free Cu phase, structure, porosity, shape of the pore, tensile property, thermal expansion coefficient and surface roughness were measured with respect to the sintered body obtained.
- a test piece was sampled from the sintered body. After polishing the cross section of the test piece was observed with Electron Probe Micro-Analyzer, and the content of the free Cu phase was measured using an image analysis software. After the cross section of the test piece was etched by Nital acid or marble etching, the structure was observed and the structure of the matrix was identified.
- the porosity was determined by converting the density of the sintered body measured by the Archimedes method into the volume % of pores.
- Shape of the pores was determined by measuring the amount of the fully connected pores in the sintered body.
- the pores were decided to be isolated or partially connected when the value defined by [(the amount of the fully connected pores)/(total amount of the pores)] ⁇ 100 (%) is 50 or less, while the pores were decided to be continuous when the value exceeds 50.
- the sintered body was immersed in liquid wax for 60 minutes, and the amount of the fully connected pores was determined by measuring the amount of permeated wax after degreasing the permeated wax. The total amount of the pore was determined by converting the density of the sintered body measured by the Archimedes method into the porosity.
- tensile strength ratio is defined as (tensile strength of the sintered body)/(tensile strength of ADC 12 aluminum alloy).
- the thermal expansion coefficient was measured the average thermal expansion coefficient from room temperature to 200° C.
- the surface roughness Rz ( ⁇ m) was measured with a needle-probe type surface roughness meter according to JIS B0601-1994.
- the stainless steel powder shown in Table 1 was used instead of the pure iron powder (A) in some of the sintered bodies.
- the stainless steel powder used was (B) a ferritic stainless steel powder (SUS 430) or (C) martensitic stainless steel powder (SUS 410L).
- the sintered bodies were produced by further blending in the mixed powder at least one powder selected from the group consisting of (a) Cr powder, (b) Mo powder, (c) W powder, (d) Fe—Mo powder, (e) Fe—Cr powder or (f) Fe—W powder.
- the iron based sintered body obtained as described above was mounted at a prescribed site of the casting mold of the bearing 3 of an internal combustion engine as a reinforcing member 1 as shown in FIG. 2 .
- the iron based sintered body was not preheated, or preheated at 200° C. before mounting on the casting mold.
- the molten aluminum alloy JIS ADC12
- JIS ADC12 molten aluminum alloy
- a tensile strength test piece including the interface between the sintered body and aluminum alloy was sampled from the bearing of the internal combustion engine obtained to measure the tensile strength.
- the tensile strength test piece was sampled in the direction containing the interface that is vertical to the axis of the test piece.
- the tensile strength ⁇ was evaluated as a bonding strength ratio relative to the desired interface strength ⁇ E , ( ⁇ / ⁇ E ).
- ⁇ E represents the interface strength between aluminum plated cast iron being enveloped in the aluminum alloy by casting and aluminum ally.
- a test piece including the sintered body was sampled from the bearing of the internal combustion engine, and the average thermal expansion coefficient was measured from room temperature to 200° C. using a thermal expansion coefficient measuring apparatus.
- All the samples in the examples of the invention show a tensile strength ratio of as high as 1.0 or more, and a bonding strength ratio of as high as 1.0 even if no preheating or preheating at a low temperature before enveloped casting in the aluminum alloy was conducted.
- the thermal expansion coefficient of the bearing member after enveloping in the aluminum alloy by casting is 15.0 ⁇ 10 ⁇ 6 /° C. or less in the examples of the invention, which is close to the thermal expansion coefficient of the iron based material.
- the tensile strength ratio is low
- the bonding strength ratio is low
- the thermal expansion coefficient is large in the samples in the comparative examples that are out of the range of the invention. Consequently, the thermal expansion coefficient of the bearing in which the iron based sintered body is enveloped by casting, cannot be suppressed when the internal combustion engine is in operation to fail in properly maintaining the change of clearance between the bearing and the crank shaft, thereby involving a risk of generating noise and vibration.
- the invention is able to exert industrially remarkable effects such that the iron based sintered body of the invention having excellent mechanical properties such as a high tensile strength as compared with light metal alloys such as an aluminum alloy, and having excellent in enveloped casting property in the light metal alloy can be cheaply and readily produced.
- the iron based sintered body of this invention is excellent in the adhesive property and has high the boding strength with the light metal such as an aluminum alloy so that the interface between the light metal and the sintered body is bonded without leaving any gaps after enveloped casting in the light metal. Furthermore, the iron based sintered body of the invention can maintain a high strength and low thermal expansion coefficient relative to the light metal alloy even after enveloped casting in the light metal alloy.
- the iron based sintered body of the invention requires no preheating, or preheating at a low temperature of as low as about 200° C., before being enveloped in the light metal alloy by casting. Consequently, the production process of the member may be simplified to enable the production cost of the internal combustion engine members to be remarkably reduced as compared with the usual process. In addition, there is another benefit that the change of clearance between the bearing and the crank shaft may be properly maintained during operation of the internal combustion engine, when the iron based sintered body of this invention is enveloped in the bearing of the internal combustion engine by casting.
Abstract
An iron based sintered body suitable for being enveloped in a light metal alloy such as an aluminum alloy by casting, and a method for producing the same. A mixed powder is prepared by mixing an iron based powder, a copper powder and a graphite powder blended so that the Cu content and the C content are 5 to 40% by mass and 0.5 to 2.5% by mass, respectively, in the mixed powder. A lubricant powder and a fine particle powder for improving machinability may be further added in the mixed powder. Then, the mixed powder is filled into a mold formed to a green compact, and is sintered into a sintered body so that the sintered body has a desired average thermal expansion coefficient. The surface of the sintered body may be adjusted to have a surface roughness Rz of 10 to 100 μm optionally by applying a shot blast treatment or by a shot blast treatment and an additional steam treatment. This process permits the sintered body to be enhanced in adhesive property and bonding strength while being improved in enveloping casting property when the sintered body is enveloped in the light metal alloy by casting. A martesitic stainless steel powder or ferritic stainless steel powder may be used instead of the pure iron powder, or Cr, Mo and W powders may be further blended.
Description
- This application is a division of U.S. patent application Ser. No. 10/743,325, filed Dec. 23, 2003, which claims priority to Japanese patent application JP 374650/2002, filed Dec. 25, 2002, the entire disclosures of which are herein incorporated by reference.
- 1. Field of the Invention
- The invention relates to an iron based sintered body, particularly to an iron based sintered body excellent in enveloped casting property in a light metal alloy. The iron based sintered body is used as being enveloped in a light metal alloy member such as an aluminum alloy by casting.
- 2. Description of the Related Art
- Automobile parts made of an aluminum alloy as a kind of light metal alloys are widely used for making the automobile parts lightweight and for enhancing heat-release ability thereof. However, the aluminum alloys are insufficient in material characteristics as automobile structural members including poor mechanical properties such as strength, wear resistance and rigidity as well as high thermal expansion coefficient as compared with usually used cast iron.
- For improving the material characteristics of the aluminum alloy members, different kind of materials are enveloped in the aluminum alloy member by casting such as, for example, gravity casting and die casting, or the aluminum alloy member is compounded with different kind of materials.
- For example, Japanese Patent Application Laid-Open (JP-A) No. 60-219436 proposes an engine block having a bearing member of an aluminum alloy housing cap which is formed by enveloping an iron based material by casting. The aluminum alloy housing cap is attached under a main body of an aluminum alloy cylinder block. According to the art described in JP-A No. 60-219436, the mechanical strength is enhanced to an extent not attainable by using only the aluminum alloy with a large improvement of rigidity, and a proper amount of the clearance change by a difference of the thermal expansion coefficient between the bearing and the crank shaft is maintained.
- Japanese Utility Model Application Laid-Open (JP-U) No. 63-150115 proposes a crank shaft supporting member of an internal combustion engine made of a light metal alloy. The inside of a portion of the supporting member partitioned with a center lines of bolt holes for mounting on a cylinder block and a curved crank journal supporting surface is reinforced with reinforcing fibers.
- JP-A 2001-276961 describes an art for producing a composite member impregnated with an aluminum alloy by a casting method, wherein molten aluminum alloy is allowed to permeate into a porous metal premolded body containing 10 to 40% by weight of chromium in iron or iron based alloy with a given time lag after completing injection of molten aluminum.
- Japanese Patent Application Publication (JP-B) No. 2-30790 proposes a method for producing an aluminum alloy casting by applying an intermetallic compound forming treatment, wherein a porous metal body is placed in a mold, the porous metal body is enveloped in an aluminum alloy by casting by a high pressure solidification casting method, and a layer of a compound between aluminum and metal element of the porous metal body is formed by heating at 450 to 550° C. According to the art described in JP-B No. 2-30790, a high bonding strength between the porous metal body and aluminum alloy is obtained with improved durability.
-
- (1) An iron based sintered body having a composition comprising, in % by mass, 0.5 to 2.5% of C, 5 to 40% of Cu, and the balance being Fe and inevitable impurities, a structure containing pores and free Cu phases dispersed in a matrix, an average thermal expansion coefficient from room temperture to 200° C. of 13.5×10−6/° C. or less, and a surface roughness Rz of 10 to 100 μm, and being excellent in an enveloped casting property in a light metal alloy.
- (2) The iron based sintered body in the above item (1), in which the surface is subjected to a shot blast treatment.
- (3) The iron based sintered body in the above item (2), in which the surface is further subjected to a steam treatment after the shot blast heatment.
- (4) The iron based sintered body in any one of the above items (1) to (3), in which the matrix has a pearlite structure.
- (5) The iron based sintered body in any one of the above items (1) to (4), in which the structure further comprises free graphites dispersed in the matrix.
- (6) The iron based sintered body in any one of the above items (1) to (5), in which the pores are isolated each other or are partially connected each other.
- (7) The iron based sintered body in any one of items (1) to (6), in which a volume ratio of the pores relative to a total volume of the sintered body is 5 to 35% by volume.
- (8) The iron based sintered body in any one of the above items (1) to (7), in which the structure further comprises 0.1 to 5% by mass of fine particles for improving machinability having a particle diameter of 150 μm or less and comprising at least one element selected from the group consisting of MnS, CaF2, BN and enstatite.
- (9) The iron based sintered body in any one of the above items (1) to (8), in which the composition comprises in % by mass, an amount of 40% or less in total of at least one element selected from the group consisting of 30% or less of Cr, 10% or less of Mo, 3% or less of Ni, 3% or less of Si, 2.5% or less of Mn, 5% or less of V, 5% or less of Ti, 3% or less of Nb and 5% or less of W.
- (10) The iron based sintered body in an item (9), in which the matrix has any one of a bainite structure, a martensite structure and a mixed structure thereof.
- (11) The iron based sintered body in any one of the above items (1) to (10), having a groove formed on any one of end faces and side faces or both.
- (12) The iron based sintered body in any one of the above items (1) to (11), in which the thermal expansion coefficient after being enveloped in an aluminum alloy by casting is 15.0×10−6/° C. or less as an average thermal expansion coefficient from room temperature to 200° C.
- (13) A light metal alloy member enveloping the iron based sintered body according any one of the above items (1) to (12) by casting.
- (14) A method for producing an iron based sintered body used for being enveloped in a light metal alloy by casting comprising the steps of preparing mixed powder by blending an iron based powder, a copper powder, a graphite powder and a lubricant powder; filling the mixed powder into a mold; forming a green compact by press-molding; and forming a sintered body by sintering the green compact, wherein a pure iron powder is used as the iron based powder, the copper powder and the graphite powder are blended so that the Cu content is 5 to 40% by mass and C content is 0.5 to 2.5% by mass relative to the total amount of the iron based powder, the copper powder and graphite powder in the mixed powder, at least any one of the molding condition of the green compact and sintering condition of sintering is controlled so that the average thermal expansion coefficient of the sintered body is 13.5×10−6/° C. or less from room temperature to 200° C.; and the surface roughness Rz is adjusted to 10 to 100 μm.
- (15) The method for producing the iron based sintered body in the above item (14), in which any one of a ferritic stainless steel powder, a martensitic stainless steel powder, pure iron powder and ferritic stainless steel powder, pure iron powder and a martensitic stainless steel powder is used as the iron based powder, instead of the pure iron powder.
- (16) The method for producing the iron based sintered body in any one of the above item (14) and (15), wherein further comprises a step of applying a steam treatment after the shot blast treatment.
- (17) The method for producing the iron based sintered body in any one of the above item (14) to (16), wherein the mixed powder contains, relative to the total amount of the mixed powder of iron based powder, copper powder, graphite powder and fine particle powder for improving machinability in the mixed powder, 0.1 to 5% by mass of the fine particle powder for improving machinability comprising at least one element selected from the group consisting of MnS powder, CaF2 powder, BN powder and enstatite powder with a particle diameter of 150 μm or less.
- (18) The method for producing the iron based sintered body in any one of the above items (14) to (17), wherein the mixed powder is further blended any one of a Cr powder, Mo powder, W powder, Fe—Cr powder, Fe—Mo powder and Fe—W powder is blended, alone or in combination, as an alloy element powder so that the mixed powder comprises, in % by mass, 40% or less in total of at least one element selected from the group consisting of 30% or less of Cr, 10% or less of Mo, 3% or less of Ni, 3% or less of Si, 2.5% or less of Mn, 5% or less of V, 5% or less of Ti, 3% or less of Nb and 5% or less of W relative to the total amount of iron based powder, copper powder, graphite powder, fine particle powder for improving machinability and alloy element powder in the mixed powder.
- (19) The method for producing the iron based sintered body in any one of the above items (14) to (18), wherein a groove is formed further on any one of end faces and side faces or both, of the green compact in the press-molding step.
- (20) The method for producing the iron based sintered body in any one of the above items (14) to (19), wherein further grooves are formed on any one of end faces and side faces or both, of the green compact in the press-molding and in a succeeding machining step.
- (21) The method for producing the iron based sintered body in any one of items (14) to (18), wherein a groove is formed further on any one of end faces and side faces or both, of the sintered body by machining after sintering.
- (22) The method for producing the iron based sintered body according to claim 14, wherein the surface roughness Rz is adjusted by applying a shot blast treatment to the sintered body.
-
FIGS. 1A and 1B schematically show examples of the shape of the iron based sintered body used in the examples and -
FIG. 2 schematically shows the structure in the vicinity of the bearing of the internal combustion engine used in the examples. - The art described in JP-A 60-219436 involved a restriction in designing arising from a problem that it is difficult to join the iron based material and an aluminum alloy without leaving any gaps, in addition to the problems that selection of iron based materials is necessary for controlling the bearing to have a desired thermal expansion coefficient. It is also a problem that production cost is forced to rise due to a requirement that the iron based material and aluminum alloy having different hardness with each other should be simultaneously machined. Furthermore, the iron based material which is enveloped by casting should be machined with high precision for arranging the iron based material at a desired position in a casting mold with high precision, which lead to additional increase of the production cost. A complex process is required for surface treatment such as aluminum plating on the surface of the iron based material in order to join the iron based material and aluminum alloy without any gaps, which leads to a further increase of the production cost.
- In the art disclosed in JP-U No. 63-150115, it is a problem that the condition for compounding the reinforced fibers is quite severe although reinforced fibers are not exposed to the outer surface. For compounding the reinforced fibers which are ceramic or metal fibers, by impregnation of the aluminum alloy, it is required that the fibers should be heated at a high temperature, and a molten aluminum alloy should be injected under a high pressure. Consequently, the production cost is forced to be increased while making the cast process complex and difficult. A desired strength of the member cannot be ensured when the density of the reinforcing fibers is decreased for making the composite process easy. The reinforcing fibers are readily broken to make handling before enveloping casting difficult. In addition, it is a problem that the machinability of the composite member is decreased because the reinforced fiber is a porous material. The quite expensive reinforced fiber also leads to a large increase of the production cost of the sintered body.
- When a composite member impregnated with the aluminum alloy is produced by using a porous metal molded body disclosed in JP-A No. 2001-276961, it is required for the aluminum alloy to be impregnated deep into the porous metal molded body for compounding, in order to stably obtain and satisfactory characteristics. For this purpose, the porous metal molded body should be preheated at a high temperature.
- The production cost is also forced to be increased in the art disclosed in JP-B No. 2-30790, since a composite production process is necessary for an intermetallic compound forming treatment.
- When the porous sintered body is enveloped in light weight metal alloy by casting, it is generally known that impregnation state of the molten light metal alloy after enveloping casting largely affects mechanical and physical properties of the resultant composite. Accordingly, cast conditions are often restricted in order to reduce the effect of impregnation state of the molten light metal alloy after enveloping casting.
- An object of the present invention is to solve the problems in the conventional art described above, and to provide an iron based sintered body excellent in enveloped casting properties in the light metal alloy and a method for producing the same. The iron based sintered body as an object of the invention is low in price and has a higher strength than a light metal alloy such as an aluminum alloy while having good machinability. Furthermore, the iron based sintered body which is an object of the invention is able to have a high bonding strength with the light metal alloy and has a higher strength and a lower thermal expansion coefficient than the light metal alloy after being enveloped in the light metal alloy such as an aluminum alloy by casting. Another object of the invention is to simplify the production process of members using the iron based sintered body, and to provide an iron based sintered body that is responsible for reducing the material cost.
- For attaining the objects above, the inventors have made intensive studies on various factors affecting on enveloped casting property in the light metal alloy such as the aluminum alloy. The inventors have found that the enveloped casting property in the light metal alloy of the iron based sintered body and the bonding strength between the iron based sintered body and the light metal alloy is remarkably improved by allowing the iron based sintered body to have a structure containing a free Cu phase dispersed in the matrix, and by adjusting the surface roughness of the iron based sintered body in a specified range by applying a shot blast treatment or further applying a steam treatment.
- The present invention have been completed based on the discoveries above and further studies.
- The iron based sintered body of the present invention has a composition of the matrix comprising, in % by mass, 0.5 to 2.5% of C and 5 to 40% of Cu, or further containing 40% or less in total of the one or more elements selected from the group of consisting of 30% or less of Cr, 10% or less of Mo, 3% or less of Ni, 3% or less of Si, 2.5% or less of Mn, 5% or less of V, 5% or less of Ti, 3% or less of Nb and 5% or less of W and the balance being Fe and inevitable impurities.
- The reason of restriction of the composition of the iron based sintered body will be described below. In the composition, “% by mass” is abbreviated as “%” hereinafter.
- C: 0.5 to 2.5%
- C is an element for enhancing the strength and hardness of the sintered body, and 0.5% or more of C is required for ensuring the strength and for forming a matrix having a pearlite structure excellent in machinability. However, coarse carbide is formed when the content of C exceeds 2.5% to result in a decrease of machinability. Accordingly, the content of C is restricted in the range of 0.5 to 2.5%.
- Cu: 5 to 40%
- Cu enhances the strength of the iron based sintered body by solid solution in the matrix. In addition, Cu is precipitated as a free Cu phase in the matrix, and reacts with the light metal alloy when the iron based sintered body is enveloped in the light metal alloy by casting. Thereby, the bonding strength between the iron based sintered body and light metal alloy is increased. Substantially the precipitation of the free Cu phase is not observed when the Cu content is less than 5% to fail in obtaining a desired bond strength. When the content of Cu exceeds 40%, on the other hand, mechanical properties such as strength is decreased. Accordingly, the content of Cu is restricted in the range of 5 to 40%, preferably in the range of 10 to 30%.
- 40% or less in total of one or more elements selected from the group consisting of 30% or less of Cr, 10% or less of Mo, 3% or less of Ni, 3% or less of Si, 2.5% or less of Mn, 5% or less of V, 5% or less of Ti, 3% or less of Nb and 5% or less of W
- Cr, Mo, Ni, Si, Mn, V, Ti, Nb and W are elements for enhancing the strength of the iron based sintered body, and at least one of them may be added, if necessary. However, when more than 30% of Cr, 10% of Mo, 3% of Ni, 3% of Si, 2.5% of Mn, 5% of V, 5% of Ti, 3% of Nb and 5% of W are added, sintering becomes difficult and the strength of the iron based sintered body is decreased. Particularly, when Cr, V and W exceeding the above contents are added, machinability is decreased as a result of coarsening of carbides. The content of silicone oxide increases by adding Si in an content exceeding the above content to result in a decrease of the melting point as well as deterioration of machinability. When the total content of these elements exceeds 40%, the strength is decreased since the alloy elements are difficult to be uniformly distributed. Cr, Mo, Si, V, Ti, Nb and W are suitable for controlling the thermal expansion coefficient of the iron based sintered body, since these elements have smaller thermal expansion coefficients than Fe.
- The balance except the components above is Fe and inevitable impurities in the composition of the matrix of the iron based sintered body of the present invention.
- The iron based sintered body of the invention has the composition as described above and further between of the porosity, the matrix structure and free Cu phases dispersed in the matrix. Free graphite phases may be dispersed in the matrix with a volume ratio of 2% or less.
- Preferably, the matrix has a pearlite structure in the iron based sintered body of the present invention, since the pearlite structure of the matrix permits machinability of the sintered body to be improved. The matrix structure may be a sorbite or troostite structure instead of the pearlite structure from the view point of machinability. A bainite structure, a martensite structure and a mixed structure thereof may be also acceptable without any problems.
- The free Cu phase dispersed in the matrix preferably accounts for 5 to 30% in volume ratio. The volume ratio of the free Cu phase of as small as less than 5% results in a decrease of the bonding strength since a small amount of an intermetallic compound of Cu and the light metal alloy is formed. When the volume ratio of the free Cu phase is as large as more than 30%, on the other hand, the bonding strength is rather decreased since the strength of the iron based sintered body is reduced to below the strength of the light metal alloy.
- Increasing the volume ratio of the free Cu phase dispersed in the matrix permits the intermetallic compound to be formed by a reaction of the molten light metal alloy with free Cu phase when the sintered body is enveloped in the light metal alloy by casting. According to this mechanism, many bonding points are formed and a high bonding strength may be obtained even if the molten light metal alloy does not impregnate deep into the iron based sintered body.
- While the iron based sintered body contains many pores, they are preferably formed as isolated each other or partially connected pores. The “partially connected pores” as used herein refers to pores which are connected each other or one another, but are not connected with more pores. The term “isolated pores or partially connected pores” as used herein means that the value defined by [(the volume of fully connected pores)/(the total volume of pores)×100 (%)] is 50 or less. The pores are considered to be continuous when the value defined above is larger than 50. The total volume of the pores may be determined by converting the density measured by the Archimedes method. The volume of the fully connected pores can be determined by allowing a wax to permeate into the sintered body by immersing the sintered body in a liquid wax for 60 minutes, and by calculating the changes of the weight before and after permeation.
- The isolated pores or partially connected pores can prevent the molten alloy from impregnating deep into the iron based sintered body when the sintered body is enveloped in the alloy by casting. Consequently, the characteristics of the iron based sintered body is less deteriorated by impregnation of the light metal alloy to enable the strength and thermal expansion coefficient inherent to the iron based sintered body to be maintained.
- The porosity of the iron based sintered body of the invention is preferably 5 to 35% by volume. A large molding pressure is required for press-molding when the porosity is less than 5% by volume. Accordingly, the process is economically disadvantageous since a large size molding machine is necessary while decreasing productivity. When the porosity exceeds 35% by volume, on the other hand, the cast light metal alloy impregnates so deep into the iron based sintered body that characteristics of the iron based sintered body is deteriorated. The porosity is determined by measuring the density of the sintered body by the Archimedes method followed by converting into the volume % of the pores.
- Fine particles for improving machinability are preferably dispersed in the matrix having above mentioned composition of the iron based sintered body of the invention for improving the machinability. Preferably, the dispersed fine particles for improving machinability are at least one element selected from the group consisting of MnS, CaF2, BN and enstatite. Particles of MnS, CaF2, BN and enstatite are able to improve machinability, and they may be added by selecting depending on the requirements.
- The cutting resistance is maintained low by uniformly dispersing the fine particles in the matrix for improving machinability, since chips during the cutting is divided into a size determined by the distance between these fine particles.
- The fine particles for improving machinability dispersed in the matrix preferably has a particle diameter of 150 μm or less. The boundary strength is decreased when the particle diameter of the fine particles for improving machinability exceeds 150 μm. The preferable diameter of fine particles for improving machinability is in the range of 5 to 100 μm.
- The content of the fine particles for improving machinability dispersed in the matrix of the porous metal sintered body is preferably 0.1 to 5% by mass relative to the whole quantity of the mixed powder, or to the total amount of the iron based powder, copper powder, alloy element powder, graphite powder and fine particles for improving machinability. No machinability improving effect is observed when a content of the fine particles for improving machinability is less than 0.1% by mass. On the other hand, the adhesive strength of the light metal alloy to the matrix as well as the adhesive strength at the boundary are decreased when the content exceeds 5% by mass. Accordingly, the content of the fine particles for improving machinability with a particle diameter of 150 μm or less is in the range of 0.1 to 5% by mass.
- The iron based sintered body of the invention has a surface roughness Rz of 10 to 100 μm. The surface area is not sufficiently increased when Rz is less than 10 μm to fail in obtaining sufficient adhesive property and bonding strength between the sintered body and light metal alloy. On the other hand, when the surface is rough with Rz of exceeding 100 μm, size accuracy becomes insufficient and the surface layer tends to generate cracks, then the adhesive property and bonding strength is decreased.
- Preferably, the iron based sintered body of the invention has grooves on the end faces and/or side faces as shown in
FIGS. 1A and 1B in addition to having a surface roughness as described above. Forming the grooves on the end faces and/or side faces permits the surface area to be increased while further improving the adhesive property and bonding strength between the molten light metal alloy and iron based sintered body. The grooves on the end faces and/or side faces are preferably formed at the stage of compressed molding, and/or in the machining process of the green compact or the sintered body. While the shape of the groove is not particularly restricted, it is preferably V-shape or arc shape. The number of the grooves may be appropriately selected depending on the thickness, shape and size of the sintered body as shown inFIGS. 1A and 1B . - The iron based sintered body of the invention having the composition and structure as described above has an average thermal expansion coefficient of 13.5×10−6/° C. or less from the room temperature to 200° C. The iron based sintered body may have an average thermal expansion coefficient of 15.0×10−6/° C. or less even after the light metal alloy has impregnated into the partially connected pores of the iron based sintered body, provided that the original average thermal expansion coefficient of the iron based sintered body is 13.5×10−6/° C. or less from room temperature to 200° C. Consequently, the thermal expansion coefficient of the iron based sintered body of the invention comes close to the thermal expansion coefficient of an iron based crank shaft of an internal combustion engine, which is 9×10−6 to 12×10−6/K. Accordingly, the thermal expansion of the bearing during operation of the internal combustion engine can be suppressed when the iron based sintered body is enveloped in the bearing of the internal combustion engine by casting. This is effective for properly maintaining the change of clearance between the bearing and crank shaft caused by a difference of the thermal expansion coefficients between them.
- The method for producing the sintered body of the invention will be described below.
- An iron based powder, a copper powder, a graphite powder and a lubricant powder, optionally fine particle powder for improving machinability, are mixed to form a mixed powder. The mixed powder is filled in a mold to form a green compact by press-molding, or compression molding. And then, the green compact is sintered to form a sintered body.
- The iron based powder used is preferably a pure iron powder and/or a stainless steel powder. The stainless steel powder is preferably a ferritic stainless steel powder or a martensitic stainless steel powder.
- Examples of the ferritic stainless steel are SUS 430, SUS 410L and SUS 434. A representative composition thereof preferably comprises, in % by mass, 0.12% or less of C, 1.0% or less of Si, 1.25% or less of Mn, 11 to 18% of Cr and 1.25% or less of Mo, and optionally at least one element selected from the group consisting of 3% or less of Ni, 5% or less of V, 5% or less of Ti, 3% or less of Nb and 5% or less of W, and the the balance being Fe and inevitable impurities.
- Examples of the martensitic stainless steel are SUS 420, SUS 410 and SUS 416. A representative composition thereof preferably comprises, in % by mass, 0.4% or less of C, 1.0% or less of Si, 1.25% or less of Mn and 11.5 to 14% of Cr, and optionally at least one element selected from the group consisting of 3% or of Ni, 5% or less of V, 5% or less of Ti, 3% or less of Nb and 5% or less of W, and the balance being Fe and inevitable impurities.
- A pure copper powder is preferably used as the raw material of the copper powder. The copper powder is added so that the content of Cu in the mixed powder is 5 to 40% by mass relative to the total content of the iron based powder, alloy element powder, copper powder, graphite powder and fine particle powder for improving machinability. No precipitation of free Cu is observed when the copper content is less than 5% by mass in the mixed powder. On the other hand, mechanical properties such as strength are decreased when the copper content exceeds 40% by mass. Accordingly, the content of Cu in the mixed powder is adjusted in the range of 5 to 40% by mass, preferably in the range of 10 to 30%.
- The graphite powder is added as the alloy element for enhancing the strength of the iron based sintered body and for improving machinability by forming the matrix structure into the pearlite structure. To obtain these effects, graphite is added so that the content of C in the mixed powder becomes 0.5 to 2.5% by mass.
- The lubricant powder is added in the mixed powder for improving moldability in the compression molding process and for increasing the density of the green compact. Zinc stearate is preferable as the lubricant powder. The content of the lubricant powder in the mixed powder is preferably 0.5 to 5 parts by weight relative to 100 parts of the whole quantity of mixed powder. The whole quantity of the mixed powder is the total amount of the iron based powder, copper powder, alloy element powder, graphite powder and fine particle powder for improving machinability.
- The fine particle powder for improving machinability may be also added to the mixed powder in addition to the iron based powder, copper powder, graphite powder and lubricant powder in order to improve machinability. The fine particle powder for improving machinability is preferably at least one element selected from the group consisting of MnS, CaF2, BN and enstatite powders. The MnS, CaF2, BN and enstatite powders are able to improve machinability, and they are selectively added if necessary. The fine particles for improving machinability preferably has a particle diameter of 150 μm or less. The bondary strength decreases when the particle diameter of the fine particles powder for improving machinability exceeds 150 μm. The preferable diameter of the fine particles powder for improving machinability is in the range of 5 to 100 μm. The preferable content of the fine particle powder for improving machinability in the mixed powder is, if any, 0.1 to 5% by mass relative to the total amount of the iron based powder, copper powder, alloy element powder, graphite powder and fine particle powder for improving machinability. The machinability improving effect cannot be obtained when the content of the fine particle powder for improving machinability is less than 0.1% by mass, while the boundary strength is decreased when the content of the fine particle powder for improving machinability exceeds 5% by mass.
- Preferably, at least one of the powders selected from the group consisting of the Cr powder, Mo powder, W powder, Fe—Cr powder, Fe—Mo powder and Fe—W powder are further blended in the mixed powder above, alone or in combination, as the alloy element powder so that the total content thereof is 40% or less relative to the total amount of the iron based powder, alloy element powder, copper powder, graphite powder and machinability improving powder, whereby the mixed powder contains, in % by mass, 40% or less in total of one or more element selected from the group consisting of 30% or less of Cr, 10% or less of Mo, 3% or less of Ni, 3% or less of Si, 2.5% or less of Mn, 5% or less of V, 5% or less of Ti, 3% or less of Nb and 5% or less of W.
- Preferably, the Cr powder, Mo powder, W powder, Fe—Cr powder, Fe—Mo powder and Fe—W powder are blended for improving the strength and decreasing the thermal expansion coefficient of the sintered body so that the blending amount is 40% or less in total in the mixed powder. The alloy elements are unevenly distributed and the strength of the sintered body decreases when the blending amount of these powders exceeds 40%.
- While the mixing method is not particularly restricted, a V-mill is preferably used for economical reasons.
- The mixed powder is filled in a mold for press-molding or compression-molding to obtain a green compact having a desired shape. The press-molding conditions of the green compact is preferably adjusted so that the sintered body has an average thermal expansion coefficient of 13.5×10−6/° C. or less from room temperature to 200° C. While the method for molding the mixed powder is not particularly restricted, a press-machine is preferably used. Preferably, the shape of the mold is previously designed so that grooves are formed on side faces and/or end faces of the green compact.
- Then, the green compact is sintered at 1100 to 1250° C. to form a sintered body.
- The sintering condition is preferably adjusted so that the sintered body has an average thermal expansion coefficient of 13.5×10−6/° C. or less from room temperature to 200° C. A reducing atmosphere is preferable for accelerating the sintering process. The sintering condition is preferably adjusted so that partially liquid-phase sintering is performed in order to form a sintered body containing isolated or partially connected pores. This method permits the pores to be isolated or partially connected since the pores are plugged with the free Cu phase.
- Subsequently, the sintered body is subjected to a shot blast treatment to have a surface roughness Rz of 10 to 100 μm. The diameter of shot particles and blowing pressure are controlled for adjusting the surface roughness. The surface is cleaned by removing surface oxidation films and the free Cu phase dispersed in the matrix is exposed to the surface by applying the shot blast treatment. Consequently, wettability between the surface of the sintered body and molten light metal alloy is improved to enable the reaction between the surface and molten alloy to be enhanced. The adhesive property is improved since bonding is formed with no interface gaps between the light metal alloy and the sintered body. The boundary strength is also improved due to an additional anchor effect as a result of the improvement of the adhesive property. The pores exposed to the surface are crushed by applying the shot blast treatment to enable the molten light metal alloy to be prevented from permeating into the sintered body during the enveloped casting process. Accordingly, the characteristics of the sintered body itself may be maintained after enveloped casting. However, no shot blast treatment is required when the surface roughness of the sintered body satisfies the range described above after sintering.
- The steam treatment is preferably applied to the sintered body subsequent to the shot blast treatment. Preferably, the steam treatment is applied at 550 to 650° C. for 30 to 90 minutes in a steam atmosphere. An iron oxide coating film is formed on the surface and exposure of free Cu on the surface because remarkable due to this steam treatment, which further accelerates the reaction between the sintered body and molten light metal alloy to enable the interface to be bonded without leaving any gaps, thus improving the adhesive property. The pores in the vicinity of the surface of the sintered body is plugged by this steam treatment to prevent a large quantity of the molten light metal alloy from permeating deep into the sintered body by casting, and the characteristics of the iron based sintered body is maintained after the enveloped casting.
- The iron based sintered body of the invention is mounted on a corresponding site in a casting mold for forming the bearing of the internal combustion engine, and a light metal alloy member is produced by a high pressure die-casting by injecting the molten light metal alloy, for example a molten aluminum alloy, into the casting mold. The light metal alloy member is processed into a final product by machining it into a prescribed size.
- The iron based sintered body produced by the method as described above is mounted on a corresponding site in a casting mold, and the light metal alloy member is produced by the high pressure die-casting by injecting the molten light metal alloy. Preheating at a temperature of as high as 500 to 550° C. that has been inevitable in the conventional iron based sintered body is no more required in the iron based sintered body according to the invention. Instead, preheating at room temperature or up to 200° C. is sufficient for the iron based sintered body of the invention. The molten light metal alloy can be injected with good circulation into the casting mold with the iron based sintered body of the invention without preheating or with preheating at a low temperature, so that good adhesive property and bonding strength between the molten light metal alloy and sintered body may be ensured. Consequently, the production process of the light metal alloy member enveloping the iron based sintered body by casting may be simplified and the manufacturing cost of the light metal alloy member may be decreased.
- A mixed powder was prepared by mixing with kneading a pure iron powder as an iron based powder, a pure copper powder as a copper powder, a graphite powder, a zinc stearate powder as a lubricant powder and a MnS powder as a fine particle powder for improving machinability was further added to the mixed powder. The blending ratio of each powder in the mixed powder is shown in Table 1.
- The mixed powder was filled in a mold and was press-molded into a green compact having a shape as shown in
FIG. 1A . Grooves being a depth of 0.5 mm were formed on end faces and side faces of a part of the green compact as shown inFIG. 1A . A green compact having a shape according to JIS Z2550 was formed as a tensile strength test piece. A green compact with a dimension of 50 mm in diameter and 15 mm in length was also prepared as a test piece for measuring a bonding strength after enveloped casting. - A sintered body was produced by liquid-phase-sintering each of the green compact under an appropriate condition depending on the content of Cu. The sintered body obtained was further subjected to a shot blast treatment and additional steam treatment, if necessary. The shot blast treatment was carried out using a steel grid prescribed in JIS G70 at a blowing pressure of 0.049 MPa (5 kgf/cm2). The steam treatment was carried out at 550° C. for 90 minutes.
- The composition, content of free Cu phase, structure, porosity, shape of the pore, tensile property, thermal expansion coefficient and surface roughness were measured with respect to the sintered body obtained.
- For measuring the content of free Cu, a test piece was sampled from the sintered body. After polishing the cross section of the test piece was observed with Electron Probe Micro-Analyzer, and the content of the free Cu phase was measured using an image analysis software. After the cross section of the test piece was etched by Nital acid or marble etching, the structure was observed and the structure of the matrix was identified.
- The porosity was determined by converting the density of the sintered body measured by the Archimedes method into the volume % of pores.
- Shape of the pores was determined by measuring the amount of the fully connected pores in the sintered body. The pores were decided to be isolated or partially connected when the value defined by [(the amount of the fully connected pores)/(total amount of the pores)]×100 (%) is 50 or less, while the pores were decided to be continuous when the value exceeds 50. The sintered body was immersed in liquid wax for 60 minutes, and the amount of the fully connected pores was determined by measuring the amount of permeated wax after degreasing the permeated wax. The total amount of the pore was determined by converting the density of the sintered body measured by the Archimedes method into the porosity.
- For measuring the tensile strength, a sample piece for the tensile strength test was prepared according to the prescription in JIS Z2550. The tensile strength was evaluated as a tensile strength ratio. Using the tensile strength of ADC12 aluminum alloy as a reference (1.0), the tensile strength ratio is defined as (tensile strength of the sintered body)/(tensile strength of ADC 12 aluminum alloy).
- The thermal expansion coefficient was measured the average thermal expansion coefficient from room temperature to 200° C. The surface roughness Rz (μm) was measured with a needle-probe type surface roughness meter according to JIS B0601-1994.
- The stainless steel powder shown in Table 1 was used instead of the pure iron powder (A) in some of the sintered bodies. The stainless steel powder used was (B) a ferritic stainless steel powder (SUS 430) or (C) martensitic stainless steel powder (SUS 410L). In some of the sintered bodies, the sintered bodies, were produced by further blending in the mixed powder at least one powder selected from the group consisting of (a) Cr powder, (b) Mo powder, (c) W powder, (d) Fe—Mo powder, (e) Fe—Cr powder or (f) Fe—W powder.
- The iron based sintered body obtained as described above was mounted at a prescribed site of the casting mold of the
bearing 3 of an internal combustion engine as a reinforcingmember 1 as shown inFIG. 2 . The iron based sintered body was not preheated, or preheated at 200° C. before mounting on the casting mold. Then, the molten aluminum alloy (JIS ADC12) was injected by high pressure die-casting to form the internalcombustion engine blocks - A tensile strength test piece including the interface between the sintered body and aluminum alloy was sampled from the bearing of the internal combustion engine obtained to measure the tensile strength. The tensile strength test piece was sampled in the direction containing the interface that is vertical to the axis of the test piece. The tensile strength σ was evaluated as a bonding strength ratio relative to the desired interface strength σE, (σ/σE). σE represents the interface strength between aluminum plated cast iron being enveloped in the aluminum alloy by casting and aluminum ally. A test piece including the sintered body was sampled from the bearing of the internal combustion engine, and the average thermal expansion coefficient was measured from room temperature to 200° C. using a thermal expansion coefficient measuring apparatus. An improvement of 30% of productivity and a decrease of 50% of the production cost were attained by omitting preheating of the sintered body, or by using the sintered body being preheated at a low temperature, when the sintered body was enveloped in the aluminum alloy by casting, as compared with the case of usual cast iron being enveloped in the aluminum alloy by casting.
- The results obtained are shown in Table 2.
- All the samples in the examples of the invention show a tensile strength ratio of as high as 1.0 or more, and a bonding strength ratio of as high as 1.0 even if no preheating or preheating at a low temperature before enveloped casting in the aluminum alloy was conducted. The thermal expansion coefficient of the bearing member after enveloping in the aluminum alloy by casting is 15.0×10−6/° C. or less in the examples of the invention, which is close to the thermal expansion coefficient of the iron based material.
- On the other hand, the tensile strength ratio is low, the bonding strength ratio is low, and the thermal expansion coefficient is large in the samples in the comparative examples that are out of the range of the invention. Consequently, the thermal expansion coefficient of the bearing in which the iron based sintered body is enveloped by casting, cannot be suppressed when the internal combustion engine is in operation to fail in properly maintaining the change of clearance between the bearing and the crank shaft, thereby involving a risk of generating noise and vibration.
- The invention is able to exert industrially remarkable effects such that the iron based sintered body of the invention having excellent mechanical properties such as a high tensile strength as compared with light metal alloys such as an aluminum alloy, and having excellent in enveloped casting property in the light metal alloy can be cheaply and readily produced. The iron based sintered body of this invention is excellent in the adhesive property and has high the boding strength with the light metal such as an aluminum alloy so that the interface between the light metal and the sintered body is bonded without leaving any gaps after enveloped casting in the light metal. Furthermore, the iron based sintered body of the invention can maintain a high strength and low thermal expansion coefficient relative to the light metal alloy even after enveloped casting in the light metal alloy. The iron based sintered body of the invention requires no preheating, or preheating at a low temperature of as low as about 200° C., before being enveloped in the light metal alloy by casting. Consequently, the production process of the member may be simplified to enable the production cost of the internal combustion engine members to be remarkably reduced as compared with the usual process. In addition, there is another benefit that the change of clearance between the bearing and the crank shaft may be properly maintained during operation of the internal combustion engine, when the iron based sintered body of this invention is enveloped in the bearing of the internal combustion engine by casting.
TABLE 1 FY3075 MIXED POWDER Other Alloy Fine Particle Powder For Element Powder Improving machinability Mixed Iron Based Kind**: Amount Graphite Copper Amount Of Powder Powder Of Blending Powder, Powder, Mean Particle Blending, No. Kind* (% By Mass) % By Mass % By Mass Kind*** Diameter μm % By Mass 1 A — 1.0 10 — — — 2 — 1.5 10 — — — 3 — 1.5 15 — — — 4 — 1.5 20 — — — 5 — 0.8 4 — — — 6 — 0.4 20 — — — 7 — 3.0 20 — — — 8 — 0.5 45 — — — 9 — 1.5 20 I 20 0.60 10 — 1.5 20 II 30 0.60 11 — 1.5 20 III 30 0.60 12 e:10 1.0 20 I 20 0.75 13 d:5, e:10 1.0 20 I 20 0.75 14 d:10 1.0 20 I 20 0.75 15 f:5 1.0 20 I 20 0.75 16 a:20 1.0 20 I 20 0.75 17 b:5 1.0 20 I 20 0.75 18 c:3 1.0 20 I 20 0.75 19 e:55 2.5 30 I 20 0.75 20 a:10, d:10, e:55 2.5 20 I 20 0.75 21 B — 2.5 30 I 20 0.75 22 C — 2.5 30 I 20 0.75 23 B e:50 2.5 30 I 20 0.75
*A: pure iron powder, B: SUS 410L, C: SUS 430
**a: Cr powder, b: Mo powder, c: W powder, d: Fe—Mo powder, e: Fe—Cr powder, f: Fe—W powder
***I: MnS, II: CaF2, III: enstatit
-
TABLE 2 FY3075 Sintered Body Composition (Content, % By Mass) Contents Of Total Particles For Mixed Contents Porosity, improving Free Cu Powder Shot Blast Steam Other Of Other % By Machinabily, Phase, Sample No. No. Treatment Treatment C Cu Elements Elements Balance Volume Shape Of Pore % By Mass Area % 1 1 Yes Yes 0.9 10 — — Fe 15 Isolated And — 8 Partially Connected 2 2 Yes Yes 1.4 10 — — Fe 14 Isolated And — 8 Partially Connected 3 3 Yes No 1.4 14 — — Fe 14 Isolated And — 13 Partially Connected 4 3 Yes No 1.4 14 — — Fe 14 Isolated And — 13 Partially Connected 5 3 Yes Yes 1.4 14 — — Fe 14 Isolated And — 13 Partially Connected 6 4 Yes No 1.4 18 — — Fe 13 Isolated And — 17 Partially Connected 7 4 Yes No 1.4 18 — — Fe 13 Isolated And — 17 Partially Connected 8 4 Yes Yes 1.4 18 — — Fe 13 Isolated And — 17 Partially Connected 9 4 Yes Yes 1.4 18 — — Fe 13 Isolated And — 17 Partially Connected 10 4 Yes Yes 1.4 18 — — Fe 4 Isolated And — 18 Partially Connected 11 4 Yes No 1.4 18 — — Fe 40 Continuous — 13 12 4 Yes No 1.4 18 — — Fe 13 Isolated And — 17 Partially Connected 13 4 Yes No 1.4 18 — — Fe 13 Isolated And — 17 Partially Connected 14 5 Yes No 0.8 4 — — Fe 10 Isolated And — — Partially Connected 15 5 Yes Yes 0.8 4 — — Fe 10 Isolated And — — Partially Connected 16 6 Yes Yes 0.4 18 — — Fe 35 Isolated And — 16 Partially Connected 17 7 Yes Yes 2.7 18 — — Fe 15 Isolated And — 18 Partially Connected 18 8 Yes No 0.5 43 — — Fe 6 Isolated And — 43 Partially Connected 19 12 Yes No 0.9 18 Cr: 6.0 6.5 Fe 15 Isolated And MnS: 0.75 16 Partially Connected 20 13 Yes No 0.9 18 Cr: 6.0, 8.5 Fe 15 Isolated And MnS: 0.75 16 Mo: 2.5 Partially Connected 21 14 Yes No 0.9 18 Mo: 5.0 5.0 Fe 15 Isolated And MnS: 0.75 16 Partially Connected 22 15 Yes No 0.9 18 W: 2.5 2.5 Fe 15 Isolated And MnS: 0.75 16 Partially Connected 23 19 Yes No 0.9 27 Cr: 30.0 30.0 Fe 34 Isolated And MnS: 0.75 21 Partially Connected 24 20 Yes No 2.4 27 Cr: 40.0, 45.0 Fe 34 Isolated And MnS: 0.75 15 Mo: 5.0 Partially Connected 25 21 Yes No 2.4 28 Cr: 8.5, 9.1 Fe 30 Isolated And MnS: 0.75 24 Si: 0.5, Partially Connected Mn: 0.1 26 22 Yes No 2.4 28 Cr: 12.0, 12.6 Fe 30 Isolated And MnS: 0.75 24 Si: 0.5, Partially Connected Mn: 0.1 27 23 Yes No 2.4 28 Cr: 30.0, 30.1 Fe 30 Isolated And MnS: 0.75 24 Si: 0.1 Partially Connected Properties After Enveloped Casting Sintered Body Tensile Tensile Properties Surface Properties Thermal Expansion Preheating Before Bonding Thermal Expansion Structure Of Roughness Tensile Coefficient ×10−8 Enveloped Casting Strength Coefficient ×10−6 Sample No. matrix*** Rz μm Strength* K−1 Temperature ° C. Ratio**** K−1 Note 1 P 32 2.9 12.2 RT 1.0 12.3 Example 200 1.1 12.3 2 P 33 2.9 12.1 RT 1.1 12.3 Example 200 1.1 12.3 3 P 26 2.8 12.6 RT 1.0 12.8 Example 200 1.1 12.8 4 P 44 2.8 12.6 RT 1.2 12.8 Example 200 1.2 12.8 5 P 43 2.7 12.6 200 1.4 12.8 Example 6 P 25 2.6 13.2 200 1.1 13.5 Example 7 P 44 2.6 13.2 200 1.2 13.5 Example 8 P 45 2.6 13.2 200 1.5 13.5 Example 9 P 74 2.6 13.2 200 1.4 13.5 Example 10 P 42 3.1 12.9 200 0.8 — Comparative Example 11 P 41 0.7 11.9 200 2.2 16.5 Comparative Example 12 P 8 2.6 13.2 200 0.9 — Comparative Example 13 P 102 2.6 13.2 200 0.9 — Comparative Example 14 P 45 3.3 11.9 200 0.5 — Comparative Example 15 P 81 3.1 11..9 200 0.8 — Comparative Example 16 P 48 0.9 12.0 200 2.1 16.3 Comparative Example 17 P 45 0.9 12.7 200 0.7 — Comparative Example 18 P 51 0.8 15.1 200 1.2 — Comparative Example 19 P 27 2.4 12.5 200 1.1 12.7 Example 20 P 26 2.2 12.2 200 1.1 12.5 Example 21 P 29 2.1 12.3 200 1.1 12.5 Example 22 P 31 2.1 12.3 200 1.1 12.4 Example 23 M 28 1.6 10.1 200 2.3 13.9 Example 24 M 24 0.8 10.4 200 2.3 12.7 Comparative Example 25 M + B 27 1.5 11.9 200 2.1 14.1 Example 26 M + B 33 1.5 11.1 200 2.1 13.9 Example 27 M 31 1.3 10.7 200 2.1 13.8 Example
*The tensile strength ratio is expressed by defining the strength of ADC 12 alloy as 1.0
***P: pearlite, B: bainite, M: martensite
****The bonding strength in the case of using aluminum plated cast iron is defined as 1.0
Claims (9)
1. A method for producing an iron based sintered body used for being enveloped in a light metal alloy by casting comprising the steps of:
preparing a mixed powder by blending an iron based powder, a copper powder, a graphite powder and a lubricant powder;
filling the mixed powder into a mold;
forming a green compact by press-molding; and
forming a sintered body by sintering the green compact; wherein
a pure iron is used as the iron based powder,
the copper powder and the graphite powder are blended so that the Cu content is 5 to 40% by mass and the C content is 0.5 to 2.5% by mass relative to the total amount of the iron based powder, the copper powder and graphite powder in the mixed powder,
at least any one of the molding condition of the compressed powder and sintering condition of the sintering is controlled so that the average thermal expansion coefficient of the sintered body is 13.5×10−6/° C. or less from room temperature to 200° C.; and
the surface roughness Rz is adjusted to 10 to 100 μm.
2. The method for producing the iron based sintered body according to claim 1 , wherein any one of a ferritic stainless steel powder, a martensitic stainless steel powder, pure iron powder and ferritic stainless steel powder, pure iron powder and martensitic stainless steel powder, is used as the iron based powder, instead of the pure iron powder for the iron based powder.
3. The method for producing the iron based sintered body according to claim 1 , further comprising applying a steam treatment after the shot blast treatment.
4. The method for producing the iron based sintered body according to claim 1 , wherein the mixed powder contains, relative to the total amount of the mixed powder, 0.1 to 5% by mass of the fine particle powder for improving machinability comprising at least one element selected from the group consisting of MnS powder, CaF2 powder, BN powder and enstatite powder with a particle diameter of 150 μm or less.
5. The method for producing the iron based sintered body according claim 1 , wherein the mixed powder is further with blended any one of a Cr powder, Mo powder, W powder, Fe—Cr powder, Fe—Mo powder and Fe—W powder, alone or in combination, as an alloy element powder,
so that the mixed powder comprises, in % by mass, 40% or less in total of at least one element selected from the group consisting of 30% or less of Cr, 10% or less of Mo, 5% or less of W, 3% or less of Si and 2.5% or less of Mn relative to the total amount of the mixed powder.
6. The method for producing the iron based sintered body according to claim 1 , wherein a groove is formed further on any one of end faces and side faces or both, of the green compact in the press-molding step.
7. The method for producing the iron based sintered body according to claim 1 , wherein a groove is formed further on any one of end faces and side faces or both, of the green compact in the press-molding and a succeeding machining step.
8. The method for producing the iron based sintered body according to claim 1 , wherein a groove is formed further on any one of end faces and side faces or both, of the sintered body by machining after sintering.
9. The method for producing the iron based sintered body according to claim 1 , wherein the surface roughness Rz is adjusted by applying a shot blast treatment to the sintered body.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US11/280,217 US20060073065A1 (en) | 2002-12-25 | 2005-11-17 | Iron based sintered body excellent in enveloped casting property in light metal alloy and method for producing the same |
Applications Claiming Priority (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2002374650A JP4115826B2 (en) | 2002-12-25 | 2002-12-25 | Iron-based sintered body excellent in aluminum alloy castability and manufacturing method thereof |
JP374650/2002 | 2002-12-25 | ||
US10/743,325 US7014677B2 (en) | 2002-12-25 | 2003-12-23 | Iron based sintered body excellent in enveloped casting property in light metal alloy and method for producing the same |
US11/280,217 US20060073065A1 (en) | 2002-12-25 | 2005-11-17 | Iron based sintered body excellent in enveloped casting property in light metal alloy and method for producing the same |
Related Parent Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US10/743,325 Division US7014677B2 (en) | 2002-12-25 | 2003-12-23 | Iron based sintered body excellent in enveloped casting property in light metal alloy and method for producing the same |
Publications (1)
Publication Number | Publication Date |
---|---|
US20060073065A1 true US20060073065A1 (en) | 2006-04-06 |
Family
ID=30768065
Family Applications (2)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US10/743,325 Expired - Lifetime US7014677B2 (en) | 2002-12-25 | 2003-12-23 | Iron based sintered body excellent in enveloped casting property in light metal alloy and method for producing the same |
US11/280,217 Abandoned US20060073065A1 (en) | 2002-12-25 | 2005-11-17 | Iron based sintered body excellent in enveloped casting property in light metal alloy and method for producing the same |
Family Applications Before (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US10/743,325 Expired - Lifetime US7014677B2 (en) | 2002-12-25 | 2003-12-23 | Iron based sintered body excellent in enveloped casting property in light metal alloy and method for producing the same |
Country Status (4)
Country | Link |
---|---|
US (2) | US7014677B2 (en) |
JP (1) | JP4115826B2 (en) |
FR (1) | FR2849448B1 (en) |
GB (1) | GB2396624B (en) |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US20070077447A1 (en) * | 2005-09-30 | 2007-04-05 | Teruyuki Oda | Iron species preform |
US20070077448A1 (en) * | 2005-09-30 | 2007-04-05 | Teruyuki Oda | Iron species preform |
JP2018024944A (en) * | 2016-08-05 | 2018-02-15 | 日本ピストンリング株式会社 | Composite having low thermal expansion coefficient and high adhesiveness |
Families Citing this family (31)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
SE0401086D0 (en) * | 2004-04-26 | 2004-04-26 | Hoeganaes Ab | Iron-based powder composition |
CA2514493C (en) * | 2004-09-17 | 2013-01-29 | Sulzer Metco Ag | A spray powder |
JP4412133B2 (en) | 2004-09-27 | 2010-02-10 | Jfeスチール株式会社 | Iron-based mixed powder for powder metallurgy |
CN102588428B (en) * | 2005-01-05 | 2014-12-10 | Ntn株式会社 | Fluid lubrication bearing device and motor having the same |
JP5214555B2 (en) * | 2005-01-06 | 2013-06-19 | Ntn株式会社 | Sintered oil-impregnated bearing |
JP4918966B2 (en) * | 2005-04-20 | 2012-04-18 | 株式会社ダイヤメット | Manufacturing method of sliding parts |
JP4918967B2 (en) * | 2005-04-20 | 2012-04-18 | 株式会社ダイヤメット | Manufacturing method of sliding parts |
US8220153B2 (en) * | 2006-05-26 | 2012-07-17 | Hitachi Powdered Metals Co., Ltd. | Production method for complex bearing |
JP5072406B2 (en) * | 2007-03-29 | 2012-11-14 | 日本ピストンリング株式会社 | Iron-based material for light metal alloy casting |
US20090162241A1 (en) * | 2007-12-19 | 2009-06-25 | Parker Hannifin Corporation | Formable sintered alloy with dispersed hard phase |
JP5558041B2 (en) * | 2009-08-04 | 2014-07-23 | Ntn株式会社 | Fe-based sintered metal bearing and manufacturing method thereof |
JP5318619B2 (en) * | 2009-03-19 | 2013-10-16 | Ntn株式会社 | Sintered metal bearing |
KR101615147B1 (en) * | 2009-03-19 | 2016-04-25 | 엔티엔 가부시키가이샤 | Sintered metallic bearing and fluid dynamic bearing device equipped with the bearing |
JP5525995B2 (en) * | 2010-10-27 | 2014-06-18 | 日立粉末冶金株式会社 | Sintered member for casting, method for producing the same, and method for casting light alloy composite member using the sintered member for casting |
JP5147025B2 (en) * | 2010-12-24 | 2013-02-20 | 富士重工業株式会社 | Iron-based preform and journal structure for forming metal matrix composites |
JP5773267B2 (en) | 2011-09-30 | 2015-09-02 | 日立化成株式会社 | Iron-based sintered sliding member and manufacturing method thereof |
CN102806350B (en) * | 2012-08-24 | 2015-05-20 | 戴初发 | Steel-copper bimetal bearing for excavating machinery |
EP2913125B1 (en) * | 2012-10-25 | 2018-10-03 | Senju Metal Industry Co., Ltd | Sliding member and production method for same |
JP6194613B2 (en) * | 2013-03-29 | 2017-09-13 | 日立化成株式会社 | Iron-based sintered alloy for sliding member and manufacturing method thereof |
JP5772998B2 (en) * | 2014-01-29 | 2015-09-02 | Jfeスチール株式会社 | Iron-based mixed powder for sintered parts with excellent machinability |
JP6480264B2 (en) | 2015-05-27 | 2019-03-06 | 株式会社神戸製鋼所 | Mixed powder and sintered body for iron-based powder metallurgy |
CN105478757B (en) * | 2016-01-07 | 2017-07-21 | 十堰同创传动技术有限公司 | The mould and forming method of single cone synchronization ring frictional layer |
JP6264622B2 (en) * | 2016-04-18 | 2018-01-24 | 株式会社ソディック | Additive manufacturing equipment |
CN110248752B (en) * | 2017-02-03 | 2022-02-01 | 日产自动车株式会社 | Sliding member and sliding member of internal combustion engine |
CN106929740B (en) * | 2017-02-04 | 2018-04-17 | 河北科技大学 | A kind of preparation method of ferrous alloy and its application in test martensite start temperature |
JP7011767B2 (en) | 2017-08-04 | 2022-02-10 | 住友電工焼結合金株式会社 | Manufacturing method of sintered parts and sintered parts |
WO2019108430A1 (en) * | 2017-11-30 | 2019-06-06 | Gkn Sinter Metals, Llc | Powder metal alloy composition for sintered powder metal insert for aluminum casting |
DE102018209267A1 (en) * | 2018-06-11 | 2019-12-12 | Federal-Mogul Nürnberg GmbH | Piston for internal combustion engines and use of a piston for internal combustion engines |
JP2021091925A (en) * | 2019-12-09 | 2021-06-17 | 国立大学法人東北大学 | Fe-BASED ALLOY HAVING EXCELLENT CORROSION PITTING RESISTANCE AND METHOD FOR PRODUCING THE SAME |
CN114453579B (en) * | 2022-01-06 | 2023-09-12 | 安徽昊方机电股份有限公司 | Preparation method of corrosion-resistant SUS420 material |
CN114700496B (en) * | 2022-03-18 | 2023-09-12 | 广东潮艺金属实业有限公司 | Preparation method of high-strength stainless steel powder |
Citations (12)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4648903A (en) * | 1984-04-10 | 1987-03-10 | Hitachi Powdered Metals Co., Ltd. | Iron base sintered, wear-resistant materials and method for producing the same |
US5007956A (en) * | 1986-04-11 | 1991-04-16 | Nippon Piston Ring Co., Ltd. | Assembled cam shaft |
US5082433A (en) * | 1989-12-20 | 1992-01-21 | Etablissement Supervis | Method for producing a cam |
US5158601A (en) * | 1991-02-14 | 1992-10-27 | Nissan Motor Co., Ltd. | Wear-resistant iron-based sintered alloy and method |
US5370725A (en) * | 1992-11-30 | 1994-12-06 | Nippon Piston Ring Co., Ltd. | Synchronizer ring |
US5534220A (en) * | 1992-04-01 | 1996-07-09 | Brico Engineering Limited | Method of sintering machinable ferrous-based materials |
US5780170A (en) * | 1994-01-10 | 1998-07-14 | Sintermetallwerk Krebsoge Gmbh | Sychronizing ring having a sintered friction coating |
US5858056A (en) * | 1995-03-17 | 1999-01-12 | Toyota Jidosha Kabushiki Kaisha | Metal sintered body composite material and a method for producing the same |
US5861565A (en) * | 1996-05-30 | 1999-01-19 | Nippon Piston Ring Co., Ltd. | Synchronizer ring |
US5900559A (en) * | 1996-08-30 | 1999-05-04 | Nippon Piston Ring Co., Ltd. | Synchronizer ring |
US6139599A (en) * | 1998-12-28 | 2000-10-31 | Nippon Piston Ring Co., Ltd. | Abrasion resistant iron base sintered alloy material for valve seat and valve seat made of iron base sintered alloy |
US6534191B2 (en) * | 2000-01-28 | 2003-03-18 | Suzuki Motor Corporation | Sintered alloy and method for the hardening treatment thereof |
Family Cites Families (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
GB1339132A (en) * | 1970-05-28 | 1973-11-28 | Brico Eng | Ferrous alloys |
JPH0610284B2 (en) * | 1986-08-09 | 1994-02-09 | トヨタ自動車株式会社 | Sintered member manufacturing method |
GB9021767D0 (en) * | 1990-10-06 | 1990-11-21 | Brico Eng | Sintered materials |
SE9201678D0 (en) * | 1992-05-27 | 1992-05-27 | Hoeganaes Ab | POWDER COMPOSITION BEFORE ADDED IN YEAR-BASED POWDER MIXTURES |
JPH06158218A (en) * | 1992-11-16 | 1994-06-07 | Mitsubishi Materials Corp | Valve guide member made of fe-based sintered alloy excellent in wear resistance |
JPH11335796A (en) * | 1998-05-19 | 1999-12-07 | Mitsubishi Materials Corp | Wear resistant piston ring of aluminum vacuum-infiltrated ferrous sintering material with excellent wear resistance |
JP2001049405A (en) * | 1999-08-13 | 2001-02-20 | Mitsubishi Materials Corp | Wear resistant piston ring made of iron base alloy excellent in high temperature wear resistance and thermal conductivity |
-
2002
- 2002-12-25 JP JP2002374650A patent/JP4115826B2/en not_active Expired - Lifetime
-
2003
- 2003-12-18 GB GB0329264A patent/GB2396624B/en not_active Expired - Fee Related
- 2003-12-23 US US10/743,325 patent/US7014677B2/en not_active Expired - Lifetime
- 2003-12-24 FR FR0315363A patent/FR2849448B1/en not_active Expired - Fee Related
-
2005
- 2005-11-17 US US11/280,217 patent/US20060073065A1/en not_active Abandoned
Patent Citations (12)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4648903A (en) * | 1984-04-10 | 1987-03-10 | Hitachi Powdered Metals Co., Ltd. | Iron base sintered, wear-resistant materials and method for producing the same |
US5007956A (en) * | 1986-04-11 | 1991-04-16 | Nippon Piston Ring Co., Ltd. | Assembled cam shaft |
US5082433A (en) * | 1989-12-20 | 1992-01-21 | Etablissement Supervis | Method for producing a cam |
US5158601A (en) * | 1991-02-14 | 1992-10-27 | Nissan Motor Co., Ltd. | Wear-resistant iron-based sintered alloy and method |
US5534220A (en) * | 1992-04-01 | 1996-07-09 | Brico Engineering Limited | Method of sintering machinable ferrous-based materials |
US5370725A (en) * | 1992-11-30 | 1994-12-06 | Nippon Piston Ring Co., Ltd. | Synchronizer ring |
US5780170A (en) * | 1994-01-10 | 1998-07-14 | Sintermetallwerk Krebsoge Gmbh | Sychronizing ring having a sintered friction coating |
US5858056A (en) * | 1995-03-17 | 1999-01-12 | Toyota Jidosha Kabushiki Kaisha | Metal sintered body composite material and a method for producing the same |
US5861565A (en) * | 1996-05-30 | 1999-01-19 | Nippon Piston Ring Co., Ltd. | Synchronizer ring |
US5900559A (en) * | 1996-08-30 | 1999-05-04 | Nippon Piston Ring Co., Ltd. | Synchronizer ring |
US6139599A (en) * | 1998-12-28 | 2000-10-31 | Nippon Piston Ring Co., Ltd. | Abrasion resistant iron base sintered alloy material for valve seat and valve seat made of iron base sintered alloy |
US6534191B2 (en) * | 2000-01-28 | 2003-03-18 | Suzuki Motor Corporation | Sintered alloy and method for the hardening treatment thereof |
Cited By (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US20070077447A1 (en) * | 2005-09-30 | 2007-04-05 | Teruyuki Oda | Iron species preform |
US20070077448A1 (en) * | 2005-09-30 | 2007-04-05 | Teruyuki Oda | Iron species preform |
US7566504B2 (en) * | 2005-09-30 | 2009-07-28 | Fuji Jukogyo Kabushiki Kaisha | Iron species preform |
US7629057B2 (en) * | 2005-09-30 | 2009-12-08 | Fuji Jukogyo Kabushiki Kaisha | Iron species preform |
JP2018024944A (en) * | 2016-08-05 | 2018-02-15 | 日本ピストンリング株式会社 | Composite having low thermal expansion coefficient and high adhesiveness |
Also Published As
Publication number | Publication date |
---|---|
GB2396624B (en) | 2005-11-02 |
FR2849448B1 (en) | 2006-12-08 |
JP2004204298A (en) | 2004-07-22 |
US7014677B2 (en) | 2006-03-21 |
GB2396624A (en) | 2004-06-30 |
FR2849448A1 (en) | 2004-07-02 |
GB0329264D0 (en) | 2004-01-21 |
JP4115826B2 (en) | 2008-07-09 |
US20040182200A1 (en) | 2004-09-23 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
US7014677B2 (en) | Iron based sintered body excellent in enveloped casting property in light metal alloy and method for producing the same | |
US11549408B2 (en) | Iron-based sintered alloy valve seat for internal combustion engine | |
JP3191665B2 (en) | Metal sintered body composite material and method for producing the same | |
US4314399A (en) | Method of producing moulds | |
US8038761B2 (en) | Iron-based sintered material and production method thereof | |
JP6688287B2 (en) | Pre-alloyed iron-based powder, iron-based powder mixture containing pre-alloyed iron-based powder, and method of manufacturing press-formed and sintered parts from the iron-based powder mixture | |
KR20010062252A (en) | valve opening/closing mechanism for internal-combustion engine | |
US20100196188A1 (en) | Method of producing a steel moulding | |
US7153337B2 (en) | Porous metal structure body and method for manufacturing the same | |
JP2010274315A (en) | Valve seat for cast-in insert of light metal alloy | |
JP6563494B2 (en) | Wear-resistant ring composite with excellent thermal conductivity | |
DE102006053018B4 (en) | Cylinder crankcase for a motor vehicle | |
JP5117085B2 (en) | Metal-ceramic composite material and manufacturing method thereof | |
JPS6233730A (en) | Wear resistant composite material | |
JP6867255B2 (en) | Complex with low coefficient of thermal expansion and high adhesion | |
JPH11189805A (en) | Fe-cu-c metal sintered compact for valve seat of internal combustion engine | |
KR102148026B1 (en) | Rolling roll manufactured by process of dissimilar materials joint and pressure-impregnation and method of manufacturing the same | |
JP2003073755A (en) | Porous metal-sintered compact for strengthening light alloy member, and manufacturing method therefor | |
JP3946055B2 (en) | Porous metal sintered body | |
KR100448465B1 (en) | Fabrication of diamond wheel for precision cutting using bronze powder-base metal bonder | |
JPH11131108A (en) | Functionally gradient fe-cu-c metallic sintered body containing ceramic particle | |
JP2008200703A (en) | Method for producing metal matrix composite | |
JP2790807B2 (en) | Composite piston | |
DE10360824B4 (en) | Iron-based sintered body with excellent properties for embedding by casting in light alloy and method for its production | |
JPH1150210A (en) | Ferrous sintered alloy part and production thereof |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
STCB | Information on status: application discontinuation |
Free format text: ABANDONED -- FAILURE TO RESPOND TO AN OFFICE ACTION |