WO2016052660A1 - Cylindre composite pour machine de moulage et procédé permettant la production de ce dernier - Google Patents

Cylindre composite pour machine de moulage et procédé permettant la production de ce dernier Download PDF

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Publication number
WO2016052660A1
WO2016052660A1 PCT/JP2015/077833 JP2015077833W WO2016052660A1 WO 2016052660 A1 WO2016052660 A1 WO 2016052660A1 JP 2015077833 W JP2015077833 W JP 2015077833W WO 2016052660 A1 WO2016052660 A1 WO 2016052660A1
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cylinder
mass
inner layer
based alloy
outer layer
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PCT/JP2015/077833
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Japanese (ja)
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内田　真継
林　清
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日立金属株式会社
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Priority to JP2016552143A priority Critical patent/JP6794833B2/ja
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D13/00—Centrifugal casting; Casting by using centrifugal force
    • B22D13/02—Centrifugal casting; Casting by using centrifugal force of elongated solid or hollow bodies, e.g. pipes, in moulds rotating around their longitudinal axis
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29C—SHAPING OR JOINING OF PLASTICS; SHAPING OF MATERIAL IN A PLASTIC STATE, NOT OTHERWISE PROVIDED FOR; AFTER-TREATMENT OF THE SHAPED PRODUCTS, e.g. REPAIRING
    • B29C45/00—Injection moulding, i.e. forcing the required volume of moulding material through a nozzle into a closed mould; Apparatus therefor
    • B29C45/17—Component parts, details or accessories; Auxiliary operations
    • B29C45/46—Means for plasticising or homogenising the moulding material or forcing it into the mould
    • B29C45/58—Details
    • B29C45/62—Barrels or cylinders
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29C—SHAPING OR JOINING OF PLASTICS; SHAPING OF MATERIAL IN A PLASTIC STATE, NOT OTHERWISE PROVIDED FOR; AFTER-TREATMENT OF THE SHAPED PRODUCTS, e.g. REPAIRING
    • B29C48/00—Extrusion moulding, i.e. expressing the moulding material through a die or nozzle which imparts the desired form; Apparatus therefor
    • B29C48/25—Component parts, details or accessories; Auxiliary operations
    • B29C48/36—Means for plasticising or homogenising the moulding material or forcing it through the nozzle or die
    • B29C48/50—Details of extruders
    • B29C48/68—Barrels or cylinders
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
    • 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
    • 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
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working

Definitions

  • the present invention relates to a composite cylinder for a molding machine that has an excellent wear resistance and corrosion resistance and has an inner layer that does not crack or peel off, and a method for producing the same.
  • Steel cylindrical cylinders are used for injection molding machines or extrusion molding machines for plastics, metal powders, and the like.
  • the inner surface of the cylinder is not only easily worn by the molding resin, the metal powder contained therein, the reinforcing material, and the additive, but also easily corroded by the corrosive gas generated from the resin and the additive.
  • a composite cylinder having a structure in which an inner layer made of a Ni-based alloy having excellent wear resistance and corrosion resistance is formed on the inner surface of a steel cylindrical outer layer by centrifugal casting.
  • Japanese Patent Application Laid-Open No. 7-90437 has a hollow cylindrical outer layer made of alloy steel and a lining excellent in wear resistance and corrosion resistance existing on the inner surface of the outer layer, and the lining is 5 to 20% Cr based on weight. 1.5 to 4% B, 0.7% or less C, 1 to 4% Si, 2% or less Mn, 5 to 20% Fe, 5 to 20% Cu, 3 to 15% W, 3 to Disclosed is a cylinder for a molding machine containing 20% Co and 2-12% Mo, the balance being made of a Ni-based alloy consisting essentially of Ni and inevitable impurities. In this molding machine cylinder, since the high-strength outer layer has sufficient durability against the expansion and contraction stress caused by the high-speed and high-pressure injection cycle, the lining is not distorted.
  • JP-A-61-52338 describes 1 to 30% Cr, 1 to 6% B, 1.5 to 25% Fe, 20% or less Co, 1 to 10% Si, and 5% or less on a weight basis.
  • a cylinder for a molding machine having a lining made of a wear-resistant and corrosion-resistant alloy containing Mn and 1% or less of C, the balance being Ni and inevitable impurities.
  • JP 61-52338 states that the alloy is 0.01 to 5% W, 0.01 to 5% V, 0.01 to 5% Nb, 0.01 to 5% Ti, and 0.01 to 5% Zr on a weight basis. It describes that it may contain at least one selected from the group consisting of:
  • a tensile stress is applied to the inner surface of the molding machine cylinder due to the pressure generated when the molding material is injected or extruded.
  • the cylinder internal pressure was about 150 MPa, but in the case of recent electric molding machines, the cylinder internal pressure often exceeds 220 MPa.
  • JP-A-7-90437 and JP-A-61-523308 it has been found that cracking and peeling occur in the inner layer of the cylinder during molding in which an internal pressure exceeding 220 mm MPa is applied. .
  • US Pat. No. 5,565,277 discloses a composite cylinder for a molding machine in which an inner layer made of nickel alloy in which tungsten carbide particles are dispersed is formed on the inner surface of a cylindrical outer layer made of microalloy steel by a centrifugal casting method.
  • the outer layer made of microalloy steel which is a kind of non-tempered steel, has high strength, and the inner layer made of nickel alloy in which tungsten carbide particles are dispersed has excellent wear resistance.
  • this compounding cylinder for a molding machine the problem that the inner layer of the cylinder is easily peeled by molding with a pressure exceeding 220 MPa has not been solved.
  • an object of the present invention is to form an inner layer excellent in wear resistance and corrosion resistance on the inner surface of the cylindrical outer layer by centrifugal casting, and the inner layer is cracked and cracked even in molding where a high pressure exceeding 220 MPa is applied to the inner surface of the cylinder. It is providing the compound cylinder for molding machines which peeling does not arise, and its manufacturing method.
  • the composite cylinder for a molding machine of the present invention is formed by forming an inner layer on the inner surface of a steel cylindrical outer layer by centrifugal casting, and the inner layer is 0.05 to 1% C, 0.5 to 6% Si, based on mass, Contains 0.1-3% Mn, 1-20% Cr, 1.5-4% B, 1-15% Co, 5-40% Fe, and 0.02-0.2% V, with the balance substantially Further, it is characterized in that it is formed of a Ni-based alloy composed of Ni and inevitable impurities.
  • the Ni-based alloy preferably further contains 0.1% by mass or less of Nb.
  • the Ni-based alloy preferably further contains 0.05% by mass or less of Mo.
  • the Ni-based alloy preferably further contains 0.1 to 4% by mass of Cu.
  • the Ni-based alloy preferably further contains 0.01 to 5% by mass of W.
  • the Ni-based alloy preferably has a structure in which the total area ratio of borides is 20 to 60%.
  • the Ni-based alloy structure of the inner layer does not contain a nickel-based dendrite having a major axis length of 0.3 mm or more.
  • the outer layer is preferably made of non-tempered steel.
  • the outer layer contains 0.3 to 0.6% C, 0.01 to 1% Si, 0.1 to 2% Mn, and 0.05 to 0.5% by mass V, with the balance being substantially Fe and inevitable impurities.
  • it is made of non-heat treated steel.
  • the non-tempered steel preferably further contains at least one selected from the group consisting of 0.01 to 1% Cr, 0.01 to 1% Cu, and 0.01 to 1% Nb on a mass basis.
  • the hardness HS of the outer layer is preferably 36-50.
  • the proof stress of the outer layer is preferably 490 to 790 MPa.
  • the difference (B ⁇ A) between the thermal expansion coefficient A of the inner layer from 20 ° C. to 600 ° C. and the thermal expansion coefficient B of the outer layer from 20 ° C. to 600 ° C. is 1 ⁇ 10 ⁇ 6 to 3 ⁇ 10 ⁇ 6 / ° C. Preferably there is.
  • the compressive residual stress in the circumferential direction on the inner surface of the inner layer is preferably 100 to 300 MPa.
  • the method of the present invention for producing the composite cylinder for a molding machine described above is that an inner layer is formed on the inner surface of a steel cylindrical outer layer by centrifugal casting, and then an average cooling rate between 900 and 600 ° C. is 10 to 200 ° C./min. It is characterized by cooling with.
  • the composite cylinder for a molding machine of the present invention comprises a high-strength steel cylindrical outer layer and an inner layer excellent in wear resistance and corrosion resistance, so that the inner layer is cracked and peeled even when molding with an internal pressure exceeding 220 MPa is performed. Can be prevented, and it has sufficient durability against molding of a resin that generates corrosive gas.
  • FIG. 4 is a SEM photograph showing the structure of a Ni-based alloy that forms the inner layer of the composite cylinder of Example 2.
  • FIG. 6 is a SEM photograph showing the structure of a Ni-based alloy forming the inner layer of the composite cylinder of Example 3.
  • 3 is an SEM photograph showing the structure of a Ni-based alloy forming the inner layer of the composite cylinder of Comparative Example 1.
  • the compound cylinder for molding machine 1 has a cylindrical outer layer 2 and an inner layer 3 formed on the inner surface by centrifugal casting, and the inner layer 3 Has a hollow portion 4 in the center.
  • the inner layer 3 formed by centrifugal casting is metal-bonded to the outer layer 2.
  • a screw hole or the like (not shown) for joining a member such as a nozzle is provided on the outer surface of the outer layer 2.
  • Ni-based alloy composition (1) Essential elements
  • the Ni-based alloy that forms the inner layer 3 has 0.05 to 1% C, 0.5 to 6% Si, 0.1 to 3% Mn, 1 to 20% Cr, 1.5 and 1.5% by mass as essential elements. It contains ⁇ 4% B, 1 ⁇ 15% Co, 5 ⁇ 40% Fe, and 0.02 ⁇ 0.2% V, with the balance consisting essentially of Ni and inevitable impurities.
  • Ni-based alloy means an alloy in which Ni is the element with the highest content.
  • Carbon (a) Carbon (C): 0.05 to 1% by mass C mainly combines with Cr to form hard carbide (and carbon boride), and improves the wear resistance of the Ni-base alloy. In addition, part of C dissolves in the base, improving the hardness and strength of the base. When C is less than 0.05% by mass, the effect of adding C is not sufficient. On the other hand, if C exceeds 1% by mass, the inner layer 3 not only becomes brittle, but the strength is lowered and cracking may occur.
  • the lower limit of the C content is preferably 0.1% by mass.
  • the upper limit of the C content is preferably 0.5% by mass.
  • Si Silicon (Si): 0.5-6% by mass Si lowers the melting point of the Ni-base alloy, increases the fluidity of the Ni-base alloy during centrifugal casting, and facilitates the formation of the inner layer 3 having a uniform thickness around the entire inner surface of the outer layer 2. In addition, Si forms an intermetallic compound with Ni and precipitates in the matrix, improving wear resistance. If Si is less than 0.5% by mass, sufficient effects cannot be obtained. On the other hand, if Si exceeds 6% by mass, the strength of the Ni-based alloy is lowered, and the inner layer 3 may be cracked.
  • the lower limit of the Si content is preferably 1% by mass.
  • the upper limit of the Si content is preferably 4% by mass.
  • Mn Manganese
  • Mn acts as a deoxidizer and suppresses casting defects due to oxygen gas generated when the inner layer 3 is solidified. If Mn is less than 0.1% by mass, sufficient effects cannot be obtained. On the other hand, Mn exceeding 3% by mass impairs the corrosion resistance of the inner layer 3.
  • the lower limit of the Mn content is preferably 0.6% by mass.
  • the upper limit of the Mn content is preferably 2% by mass.
  • the Ni-based alloy for the inner layer of the present invention contains hard boride and / or carbon boride.
  • the term “boride” includes both boride and carbon boride.
  • the Ni-base alloy for the inner layer of the present invention may contain carbide.
  • the inclusion of 1% by mass or more of Cr facilitates the formation of borides, and the inner layer 3 having sufficient hardness can be obtained.
  • Cr exceeds 20% by mass, the amount of borides becomes excessive, and the strength of the inner layer 3 decreases.
  • the preferable lower limit of Cr is 3% by mass.
  • the upper limit of the Cr content is preferably 15% by mass, and more preferably 10% by mass.
  • B 1.5-4% by mass Boron (B) lowers the melting point of the Ni-based alloy, increases the fluidity of the Ni-based alloy during centrifugal casting, and makes it easier to form the inner layer 3 having a uniform thickness around the entire inner surface of the outer layer 2.
  • B combines with Cr, Ni, Fe, V, etc. to form a high hardness boride in the structure, increasing the hardness of the inner layer 3 and improving the wear resistance. If B is less than 1.5% by mass, sufficient effects cannot be obtained. On the other hand, if B exceeds 4% by mass, the amount of borides becomes excessive, the strength of the inner layer 3 is remarkably lowered, and cracks may occur.
  • the lower limit of the B content is preferably 2.2% by mass, more preferably 2.6% by mass.
  • the upper limit of the B content is preferably 3.5% by mass, more preferably 3% by mass, and most preferably 2.95% by mass.
  • Co Cobalt
  • the lower limit of the Co content is preferably 5% by mass.
  • the upper limit of the Co content is preferably 12% by mass.
  • the lower limit of the Fe content is preferably 10% by mass, more preferably 15% by mass, most preferably 20% by mass, and particularly preferably 23% by mass.
  • the upper limit of the Fe content is preferably 35% by mass, more preferably 30% by mass.
  • V Vanadium (V): 0.02-0.2 mass% V has the effect of refining the structure of the Ni-based alloy.
  • the centrifugally cast inner layer 3 is solidified, the formation of coarse nickel-based dendrite is suppressed, the structure of the Ni-based alloy forming the inner layer 3 is made finer, and the strength of the inner layer 3 is thereby increased.
  • nickel-based dendrite means a dendrite mainly composed of nickel.
  • the dendrite leaking to the inner surface of the inner layer 3 is preferentially corroded during injection molding and becomes a recess that becomes a starting point of destruction, and the inner layer 3 is likely to crack.
  • V exceeds 0.2% by mass coarse vanadium borides are generated, the inner layer 3 is embrittled and the strength is lowered.
  • the lower limit of the V content is preferably 0.03% by mass, more preferably 0.04% by mass.
  • the upper limit of the V content is preferably 0.1% by mass.
  • Ni preferably has the following relationship with respect to the essential elements Fe and Co.
  • the Fe / Ni ratio greatly affects the thermal expansion coefficient of the Ni-based alloy. Further, as will be described later, the compressive residual stress on the inner surface of the inner layer 3 is determined by the relationship between the thermal expansion coefficient of the inner layer 3 and the thermal expansion coefficient of the outer layer 2. In order to generate a desired compressive residual stress on the inner surface of the inner layer 3, the Fe / Ni ratio in the Ni-based alloy forming the inner layer 3 is preferably set to 0.35 to 0.9.
  • the Fe / Ni ratio When the Fe / Ni ratio is less than 0.35, the Ni base alloy has an insufficient effect of decreasing the thermal expansion coefficient, the compressive residual stress on the inner surface of the inner layer 3 is insufficient, and the effect of suppressing cracking of the inner layer 3 is insufficient.
  • the Fe / Ni ratio exceeds 0.9, the Ni content is relatively lowered, and the corrosion resistance of the Ni-based alloy is undesirably lowered.
  • a more preferable lower limit of the Fe / Ni ratio is 0.5, and a more preferable upper limit is 0.7.
  • the Co / Ni ratio is preferably 0.15 to 0.5.
  • the upper limit of the Co / Ni ratio is more preferably 0.4, and most preferably 0.3.
  • Ni-base alloy forming the inner layer 3 is a group consisting of, as an optional element, 0.1% or less of Nb, 0.05% or less of Mo, 0.1 to 4% of Cu, and 0.01 to 5% of W on a mass basis. You may contain at least 1 type of element chosen from these.
  • the Nb content is preferably 0.1% by mass or less.
  • the Nb content is more preferably 0.05% by mass or less.
  • Mo Molybdenum
  • Mo 0.05% by mass or less Mo, like V, has the effect of refining the structure of the Ni-based alloy, so 0.05% by mass or less of Mo may be added to the Ni-based alloy.
  • Mo exceeds 0.05 mass%, not only the inner layer 3 becomes brittle but also the strength decreases.
  • the Mo content is more preferably 0.03% by mass or less.
  • the lower limit of the Cu content is more preferably 0.5% by mass, and the upper limit of the Cu content is more preferably 2% by mass.
  • the lower limit of the W content is more preferably 0.1% by mass, and the upper limit of the W content is more preferably 3% by mass.
  • Inevitable impurities As an inevitable impurity element, phosphorus (P), sulfur (S), aluminum (Al), titanium (Ti), etc. may be included in a total amount of 0.1% by mass or less.
  • Total area ratio of boride Inner layer 3 formed by centrifugally casting an Ni-based alloy having the above composition on the inner surface of cylindrical outer layer 2 has a total area ratio of boride of 20- It is preferred to have a 60% dispersed structure.
  • the metal elements constituting the boride are mainly Ni, Cr, V, Fe, W and the like.
  • the total area ratio of borides is less than 20%, the Ni-based alloy does not exhibit sufficient wear resistance.
  • the total area ratio of borides exceeds 60%, the Ni-based alloy is too hard and the toughness is insufficient.
  • a more preferable lower limit of the total area ratio of borides is 30%, and a more preferable upper limit is 55%.
  • the total area ratio of borides was binarized using the image processing software of Image-Pro Plus ver. 7.0 manufactured by Media Cybernetics, and SEM photographs of Ni-based alloys were binarized. It was determined by judging as a boride or a carbonized boride.
  • the coarse nickel-based dendrite is a dendritic crystallized product 10 as shown in FIG. 4 and has a long axis (stem) length DL of 0.3 mm or more.
  • the dendrite is preferentially corroded in the injection molding process, and a recess is formed on the inner surface of the inner layer 3. Since stress concentrates in the recess, it tends to be the starting point of fracture.
  • the inner layer 3 preferably has a circumferential compressive residual stress of 100 to 300 MPa on its inner surface. If the circumferential compressive residual stress on the inner surface of the inner layer 3 is less than 100 MPa, the inner layer 3 is likely to crack during molding. On the other hand, if the compressive residual stress exceeds 300 MPa, an excessive circumferential tensile residual stress is applied to the outer layer 2 near the boundary between the inner layer 3 and the outer layer 2, and the outer layer 2 may be fatigued and the inner layer 3 may be peeled off. .
  • the outer layer 2 is preferably formed of high-strength steel so as to hold the inner layer 3 firmly and prevent cracking of the inner layer 3 during molding.
  • high strength steel carbon steel or non-tempered steel is preferable, and non-tempered steel is particularly preferable.
  • Carbon steel itself may be a known one, for example, carbon steel containing 0.25 to 0.6% by mass of carbon is preferable.
  • the general composition of such a carbon steel contains 0.25 to 0.6 mass% carbon, 0.15 to 0.35 mass% silicon, 0.60 to 0.90 mass% manganese, with the balance being substantially Fe and inevitable impurities. Become.
  • Non-tempered steel containing alloy elements such as V has excellent proof stress and toughness without heat treatment (tempering treatment), so steels such as S45C and SCM440 (centrifugal casting to obtain sufficient proof stress)
  • the manufacturing cost of the composite cylinder can be reduced more than heat treatment is required later.
  • Non-tempered steel forming outer layer 2 is generally 0.3 to 0.6% by mass of C, 0.01 to 1% Si, 0.1 to 2% Mn, and 0.05 to 0.5% by mass. V is contained, and the balance is substantially composed of Fe and inevitable impurities.
  • the non-tempered steel may further contain at least one element selected from the group consisting of 0.01 to 1% by mass of Cr, 0.01 to 1% by mass of Cu, and 0.01 to 1% by mass of Nb as optional elements.
  • Si 0.01-1% by mass Si dissolves in the base structure and has the effect of strengthening the non-tempered steel.
  • Si content is 0.01% by mass or more, a sufficient reinforcing effect is recognized.
  • Si exceeds 1% by mass, the toughness of the non-tempered steel decreases.
  • Mn 0.1-2% by mass Mn is an element that strengthens non-heat treated steel. When the Mn content is 0.1% by mass or more, a sufficient reinforcing effect is recognized. On the other hand, when Mn exceeds 2% by mass, the toughness of the non-tempered steel decreases.
  • V 0.05 to 0.5 mass% V precipitates as fine carbides in the non-tempered steel and improves the proof stress of the non-tempered steel.
  • V content is 0.05% by mass or more, a sufficient yield strength improving effect is recognized.
  • the toughness of non-tempered steel decreases when V exceeds 0.5% by mass. If the toughness of the outer layer 2 is too low, cracks generated in the inner layer 3 are likely to propagate to the outer layer 2.
  • Optional elements 0.01-1% by mass Cr is an element that strengthens non-heat treated steel. When the Cr content is 0.01% by mass or more, a sufficient reinforcing effect is recognized. On the other hand, if Cr exceeds 1% by mass, the toughness of the non-tempered steel decreases.
  • Cu 0.01-1% by mass
  • Cu is an element that strengthens non-heat treated steel.
  • the Cu content is 0.01% by mass or more, a sufficient reinforcing effect is recognized.
  • Cu exceeds 1% by mass, the toughness of the non-tempered steel decreases.
  • Nb 0.01-1% by mass Nb, like V, has the effect of improving the yield strength of non-tempered steel.
  • Nb content is 0.01% by mass or more, a sufficient yield strength improving effect is recognized.
  • Nb exceeds 1% by mass, toughness is reduced. If the toughness of the outer layer 2 is too low, cracks generated in the inner layer 3 are likely to propagate to the outer layer 2.
  • the outer layer 2 preferably has a hardness HS of 36-50. High hardness outer layer 2 tends to have excellent yield strength. If the hardness HS is less than 36, the yield strength of the outer layer 2 is insufficient, and cracking of the inner layer 3 tends to occur during molding. On the other hand, if the hardness HS exceeds 50, the machinability of the outer layer 2 is lowered, and screw machining becomes difficult.
  • the outer layer 2 preferably has a yield strength of 490 to 790 MPa. If the proof stress is less than 490 MPa, the fatigue strength of the outer layer 2 is insufficient, and the inner layer 3 tends to crack during molding. On the other hand, when the proof stress exceeds 790 MPa, the machinability of the outer layer 2 is lowered, and screw machining becomes difficult.
  • Thermal expansion coefficient at 600 ° C. from 20 ° C. of the outer layer 2 made of a non-heat treated steel is generally 13.5 ⁇ 10 -6 /°C ⁇ 14.5 ⁇ 10 -6 / °C .
  • the difference in thermal expansion coefficient (B ⁇ A) can be obtained by combining the outer layer 2 made of non-heat treated steel having such a thermal expansion coefficient and the inner layer 3 made of the Ni-based alloy.
  • Ni-base alloy molten metal is directly introduced into the cylindrical outer layer 2 or Ni-base alloy powder is sealed in the outer layer 2 and then melted by heating, and then cylindrical at a predetermined rotational speed with a centrifugal casting machine. By rotating the outer layer 2, the Ni-based alloy is firmly metal-bonded to the inner surface of the outer layer 2, and the inner layer 3 is formed.
  • the average cooling rate is 10 to 200 ° C./min. When the average cooling rate is less than 10 ° C./min, the proof stress of the outer layer 2 cannot be obtained sufficiently.
  • the vanadium boride that precipitates in the initial stage of solidification moves more to the inner peripheral side of the inner layer 3 due to centrifugal force.
  • the vanadium boride that suppresses the formation of dendrites is significantly unevenly distributed on the inner peripheral side of the inner layer 3. Accordingly, excessive dendrite is excessively generated on the outer peripheral side of the inner layer 3.
  • the average cooling rate exceeds 200 ° C./min, the steel forming the outer layer 2 is likely to undergo martensitic transformation or bainite transformation, the tensile residual stress of the inner layer 3 becomes excessive, and the inner layer 3 may crack. is there.
  • the preferred average cooling rate between 900-600 ° C. on the surface of the outer layer 2 is 50-150 ° C./min.
  • the cooling rate can be controlled by, for example, blast or mist spray. Further, it is preferable that the cooling rate is uniform over the entire circumference and the entire length of the cylinder 1, and the proof strength of the outer layer 2, the cracking of the inner layer 3 and the generation of dendrites are suppressed in the entire cylinder 1.
  • Cylindrical outer layers having an outer diameter of 95 mm, an inner diameter of 34 mm, and a length of 1000 mm were formed of carbon steel (S45C) and non-tempered steel, respectively.
  • Carbon steel contains 0.45% by mass of carbon, 0.25% by mass of silicon, and 0.72% by mass of manganese, with the balance being substantially composed of Fe and inevitable impurities, and heat at 20 ° C to 600 ° C.
  • the expansion coefficient was 16.0 ⁇ 10 ⁇ 6 / ° C.
  • Non-tempered steel contains 0.45% by mass of C, 0.30% by mass of Si, 1.21% by mass of Mn and 0.12% by mass of V, and the balance is substantially composed of Fe and inevitable impurities.
  • the thermal expansion coefficient from 20 ° C.
  • the outer layer made of carbon steel was used for the composite cylinders of Example 1 and Comparative Example 1, and the outer layer made of non-heat treated steel was used for the composite cylinders of Examples 2 and 3.
  • the Ni-base alloy having the composition shown in Table 1 was sealed inside each outer layer, and the openings at both ends of the outer layer were sealed with lids, and then heated to 1150 ° C. to dissolve the Ni-base alloy. Thereafter, a cylindrical inner layer having a thickness of 5 mm was formed on the inner surface of the outer layer by centrifugal casting. By performing mist cooling, the cooling rate between 900-600 ° C. on the surface of the outer layer was adjusted to 50 ° C./min, and the resulting composite cylinder was cooled to room temperature.
  • the composite cylinders of Examples 1 to 3 and Comparative Example 1 having an outer diameter of 90 mm, an inner diameter of 24 mm, and a length of 900 mm were obtained by removing the lid and machining the outer periphery and end of the outer layer.
  • the composite cylinder of Example 1 and Comparative Example 1 (using carbon steel for the outer layer) was subjected to heat treatment (tempering treatment) at 850 ° C. for 1 hour after centrifugal casting.
  • Samples TP1 with a thickness of 1.5 mm, a circumferential length of 4 mm, and an axial length of 15 mm are sampled from the inner layer part close to the joining boundary with the outer layer in each sample material.
  • the thermal expansion coefficient of was measured.
  • Table 3 shows the average thermal expansion coefficient A of the inner layer at 20 ° C to 600 ° C.
  • Table 3 also shows the average thermal expansion coefficient B of the carbon steel and non-heat treated steel at 20 ° C. to 600 ° C. as the average thermal expansion coefficient B of the inner layer at 20 ° C. to 600 ° C. of the outer layer.
  • Table 3 shows the difference (B ⁇ A) between the average thermal expansion coefficient A and the average thermal expansion coefficient B from 20 ° C. to 600 ° C.
  • the Rockwell hardness HRC of the inner layer of each test material was measured at a position of 1 mm from the junction boundary with the outer layer.
  • Table 3 shows the Rockwell hardness HRC of the inner layer.
  • each composite cylinder was machined and polished to an inner diameter of 30 mm and a thickness of 2 mm, and then a strain gauge was attached to the inner surface of the inner layer.
  • the compressive residual stress S was measured by cutting the inner layer portion to which the strain gauge was attached to a thickness of 1 mm, a circumferential length of 20 mm, and an axial length of 20 mm and releasing the stress. Table 3 shows the measurement results.
  • a test piece whose cross section was observable was cut out from the inner layer of each specimen.
  • the cross section of the inner layer was mirror-polished and etched with a nital etchant, and then SEM photographs (magnification: 20 times) were taken for the four fields of view.
  • the number of dendrites with an axial length of 0.3 mm or more per 100 mm 2 ).
  • the results are shown in Table 4.
  • SEM photographs of Examples 2 and 3 and Comparative Example 1 are shown in FIGS. 2 to 4, respectively.
  • A represents a base
  • B represents a boride
  • C represents a carbon boride.
  • Each SEM photograph was observed to determine the major axis length DL of the nickel-based dendrite 10 and the number of nickel-based dendrite 10 having a major axis length DL of 0.3 mm or more. The results are shown in Table 4.
  • the major axis length DL of the dendrite 10 is the length of the portion corresponding to the dendrite trunk as shown in FIG.
  • the Shore hardness HS of the outer layer of the cylindrical specimen was measured at the center in the longitudinal direction and at a position 5 mm away from the boundary with the inner layer. Table 5 shows the measurement results.
  • a tensile test piece TP2 corresponding to JIS No. 5 was cut out at a position close to the joining boundary with the inner layer, and the proof stress was measured using a tensile tester. Table 5 shows the measurement results.
  • Corrosion Evaluation Criteria 1 ⁇ 10 After forming 5 times, measure the inner diameter at the tip of the cylinder on the injection side (maximum corrosion) and calculate the amount of corrosion (mm) of the inner layer (D 0 -D 2 ) / 2 (where D 0 is the inner diameter of the cylinder before molding, and D 2 is the inner diameter of the cylinder after corrosion by molding).
  • ⁇ Corrosion amount was over 0.025 mm and 0.05 mm or less.
  • X Corrosion amount was more than 0.05 mm.
  • the inner layer was not cracked or peeled off by injection molding, and the wear amount and corrosion amount were small.
  • the inner layer was cracked or peeled off.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Injection Moulding Of Plastics Or The Like (AREA)
  • Extrusion Moulding Of Plastics Or The Like (AREA)

Abstract

L'invention porte sur un cylindre composite pour des machines de moulage, qui est obtenu par la formation d'une couche interne par un procédé de coulée centrifuge sur la surface interne d'une couche externe cylindrique constituée d'un acier et dans lequel la couche interne est constituée d'un alliage à base de Ni qui contient, en termes de % en masse, 0,05 à 1 % de C, 0,5 à 6 % de Si, 0,01 à 3 % de Mn, 1 à 20 % de Cr, 1,5 à 4 % de B, 1 à 15 % de Co, 5 à 40 % de Fe et 0,02 à 0,2 % de V, le reste étant constitué essentiellement de Ni et d'impuretés inévitables.
PCT/JP2015/077833 2014-09-30 2015-09-30 Cylindre composite pour machine de moulage et procédé permettant la production de ce dernier WO2016052660A1 (fr)

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Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN108237213A (zh) * 2017-12-29 2018-07-03 上海天阳钢管有限公司 一种制造双金属复合轴承坯料的工艺方法
WO2018124041A1 (fr) * 2016-12-27 2018-07-05 東洋鋼鈑株式会社 Pièce coulée et procédé de fabrication d'une pièce coulée
CN109097706A (zh) * 2018-09-20 2018-12-28 南通明月电器有限公司 一种导磁铁镍合金材料及生产工艺

Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2009113457A (ja) * 2007-11-09 2009-05-28 Hitachi Metals Ltd 成形機用シリンダ

Patent Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2009113457A (ja) * 2007-11-09 2009-05-28 Hitachi Metals Ltd 成形機用シリンダ

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2018124041A1 (fr) * 2016-12-27 2018-07-05 東洋鋼鈑株式会社 Pièce coulée et procédé de fabrication d'une pièce coulée
CN108237213A (zh) * 2017-12-29 2018-07-03 上海天阳钢管有限公司 一种制造双金属复合轴承坯料的工艺方法
CN109097706A (zh) * 2018-09-20 2018-12-28 南通明月电器有限公司 一种导磁铁镍合金材料及生产工艺

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