EP2902522A1 - Lochwerkzeugmaterial zur herstellung eines nahtlosen stahlrohrs und verfahren zur herstellung des materials - Google Patents

Lochwerkzeugmaterial zur herstellung eines nahtlosen stahlrohrs und verfahren zur herstellung des materials Download PDF

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Publication number
EP2902522A1
EP2902522A1 EP13842050.0A EP13842050A EP2902522A1 EP 2902522 A1 EP2902522 A1 EP 2902522A1 EP 13842050 A EP13842050 A EP 13842050A EP 2902522 A1 EP2902522 A1 EP 2902522A1
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EP
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Prior art keywords
piercer plug
less
heat treatment
manufacturing
plug
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EP13842050.0A
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English (en)
French (fr)
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EP2902522B1 (de
EP2902522A4 (de
Inventor
Kotaro ONA
Yuta YOKOMIZO
Yasuyoshi Hidaka
Tetsuya Nakanishi
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Nippon Steel Corp
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Nippon Steel and Sumitomo Metal Corp
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22C—FOUNDRY MOULDING
    • B22C9/00—Moulds or cores; Moulding processes
    • B22C9/22—Moulds for peculiarly-shaped castings
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B25/00—Mandrels for metal tube rolling mills, e.g. mandrels of the types used in the methods covered by group B21B17/00; Accessories or auxiliary means therefor ; Construction of, or alloys for, mandrels or plugs
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
    • C21D8/105—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
    • C21D9/085—Cooling or quenching
    • 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
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum

Definitions

  • the present invention relates to a piercer plug which is used when using the Mannesmann process to manufacture seamless steel pipe (sometimes simply referred to as a "plug"), more particularly relates to a material for piercer plug for manufacturing seamless steel pipe which is excellent in season cracking resistance and machinability and a method of manufacturing the same.
  • plants for manufacturing seamless steel pipe are increasingly dispersed and built at distant locations. Transport times are increasing etc., so from the viewpoint of obtaining inventories, piercer plugs are often stored for longer time.
  • the piercer plugs or materials for piercer plug is excellent in machinability and further can be stored for a long period of time.
  • the piercer plug surface suffers from cracks called "season cracking".
  • season cracking easily occurs in the winter season.
  • Piercer plugs suffering from "season cracking” cannot be used for manufacturing seamless steel pipe.
  • PLT 1 discloses a piercer plug which is comprised of predetermined components for raising the high temperature deformation resistance plus a large amount of at least one of Mo and W added to suppress surface decarburization and form an internal oxide type scale layer on the surface.
  • PLT 2 discloses a method of manufacturing a piercer plug which is comprised of a 3Ni-1Cr steel or other steel base member on the surface of which scale is formed, wherein the steel base member is fabricated by casting using conventional sand mold casting. Further, the method of manufacturing the same is described as improving the strength of the steel base member and having the effect of improving the scale.
  • PLT 3 like PLT 2, discloses a base member of a piercer plug which scale is formed on surface thereof and the strength of the base member is improved and there is an effect of improving the scale.
  • PLT 4 like PLT 2, discloses a piercer plug which is comprised of a base material on the surface of which a scale is formed wherein a net-like scale layer which is intertwined with the base material is formed as the layer which forms the scale layer.
  • PLT 4 discloses that by the above configuration of the scale layer, peeling or wear of the scale layer is suppressed and the piercer plug can be extended in lifetime.
  • PLT 5 discloses that by using a technique similar to PLT 4 so as to form a scale layer as an intergranular oxidation type scale layer, the adhesion with the base material becomes good, peeling or wear of the scale layer is suppressed, and the piercer plug can be extended in lifetime.
  • a coating forming technique utilizing thermal spraying is used to form a protective coating on the surface of the piercer plug to thereby promote longer lifetime of the piercer plug.
  • an object of the present invention is to solve the problem unable to be solved by the prior art of providing a material for a piercer plug which is used when manufacturing seamless steel pipe by the Mannesmann process wherein occurrence of season cracking by long term storage is suppressed, wherein machinability is also excellent, and, furthermore, and the piercer plug has the desired hardness whereby the plug body can be made longer in life.
  • the present invention was made based on these discoveries and has as its gist the following:
  • the present invention it is possible to provide a material for piercer plug for manufacturing seamless steel pipe which is used at the time of manufacturing seamless steel pipe by the Mannesmann process and which is in particular excellent in season cracking resistance and machinability.
  • C is an effective component for improving the high temperature strength, but has no effect if the content is smaller than 0.08%. Further, if over 0.3%, the hardness becomes too high and season cracking more easily occurs. Further, control of the state of precipitation of carbides also becomes difficult. Therefore, C is made 0.08 to 0.3%. If considering the variation for obtaining this effect, the lower limit is preferably 0.10%, more preferably 0.12%. Further, similarly, the upper limit is preferably 0.25%, more preferably 0.20%.
  • Si is an effective component for deoxidation, but the effect is small if smaller than 0.1%. If over 1.0%, the base material starts to deteriorate in toughness. Therefore, Si is made 0.1 to 1.0%. If considering the variation for obtaining this effect, the lower limit is preferably 0.20%, more preferably 0.30%. Further, similarly, the upper limit is preferably 0.90%, more preferably 0.80%.
  • Mn stabilizes the austenite at a high temperature. That is, it suppresses the formation of ⁇ -ferrite to suppress the drop in toughness. That effect is obtained at 0.2% or more. However, if adding more than 1.5%, the hardness becomes too high and season cracking easily occurs after piercing. Therefore, Mn is made 0.2 to 1.5%. If considering the variation for obtaining this effect, the lower limit is preferably 0.30%, more preferably 0.40%. Further, similarly, the upper limit is preferably 1.30%, more preferably 1.00%.
  • Ni has the action of improving the toughness of the quenched phase which is formed on the surface part of the plug. To obtain this effect, 0.2% or more is necessary, but the effect becomes substantially saturated at 2.0%. The above addition becomes a factor increasing the cost. Therefore, Ni is made 0.2 to 2.0%. If considering the variation for obtaining this effect, the lower limit is preferably 0.30%, more preferably 0.40%. Further, similarly, the upper limit is preferably 1.90%, more preferably 1.80%.
  • Mo and W are both effective for improving the high temperature strength and have the effect of raising the Ac1 point to reduce the quenched part at the surface after piercing. These effects are equivalent with Mo and W.
  • the effect becomes small if one or the total of both of Mo and W is less than 1.5%, so these are added to become greater than this. Further, if one or the total of both of Mo and W exceeds 8.0%, ferrite remains even at a high temperature, the strength starts to fall, and the toughness is also caused to fall. Accordingly, the total of Mo+W is made 1.5 to 8.0%.
  • the lower limit is preferably 1.7%, more preferably 2.0%.
  • the upper limit is preferably 7.5%, more preferably 7.0%.
  • the H (hydrogen) which is contained as diffusible hydrogen in the material for piercer plug is an element which aggravates the season cracking of the piercer plug, so the content has important meaning in the present invention.
  • Diffusible hydrogen is hydrogen which diffuses in the material. Hydrogen which is trapped in voids in the material etc. is not included. Further, the method of measurement of the diffusible hydrogen will be explained in the later explained examples.
  • the content of diffusible hydrogen should be as small as possible. The inventors discovered that if the diffusible hydrogen is 2 ppm or less, season cracking does not occur (see Table 5). For this reason, the content of the material for piercer plug according to the present invention is given an upper limit of 2 ppm.
  • the upper limit is preferably 1.5 ppm, more preferably 1.0 ppm or less.
  • the steel material obtained by casting contains 7 ppm or more of diffusible hydrogen.
  • the diffusible hydrogen in the material can be reduced at the time of heat treatment holding the material at a 700 to 900°C temperature range for 0.5 hour to 4 hours. Details of the dehydrogenation will be explained in the later explained method of manufacturing the same.
  • Nb, V, Cr, and Ti each 1.0% or less
  • Nb, V, and Ti have the effect of refining the crystal grains. However, if added over 1.0%, brittle phases precipitate and deterioration of the toughness is invited. Therefore, one or more of Nb, V, and Ti may be added in respectively 1.0% or less. If considering the variation for obtaining this effect, the upper limit is preferably 0.5%, more preferably 0.1%. Cr has the action of improving the toughness of the steel material and deformation resistance at a high temperature. However, from the economic viewpoint, the upper limit of the content is made 1.0%.
  • Cu is an element which stabilizes austenite and has the action of improving the toughness of the surface part of the plug which becomes austenite when held at a high temperature at the time of piercing. To obtain that effect, 0.01% or more is necessary, but the effect becomes substantially saturated at 0.5%. Therefore, Cu is made 0.5% or less. If considering the variation for obtaining this effect, the lower limit is preferably 0.01%, more preferably 0.1%. Further, similarly, the upper limit is preferably 0.5%, more preferably 0.3%.
  • the upper limit is preferably 0.05%, more preferably 0.01%.
  • Ca, Mg, and REM can all be added for the purpose of desulfurization etc. In particular, this is effective for grain refinement and improves the toughness of the steel material. However, if the contents in total exceed 0.5%, brittle phases precipitate and invite a drop in toughness. Therefore, the contents of these components were made a total of 0.5% or less. If considering the variation for obtaining this effect, the upper limit is preferably 0.2%, more preferably 0.1%.
  • the hardness of the material for piercer plug of the present invention is preferably HRC6 to 40. If becoming an over HRC40 high hardness, season cracking easily occurs. On the other hand, it falling under HRC6, the piercing lifetime of the piercer plug falls. That is, due to insufficient strength, the piercer plug is liable to greatly deform at the time of piercing-rolling.
  • the more preferable lower limit is HRC20.
  • the structure of the material for piercer plug is preferably tempered martensite and/or bainite. However, if just leaving the material for piercer plug in as-cast state, the structure will mainly become tempered martensite. By heat treatment after casting, the structure mainly becomes tempered martensite and/or bainite and the toughness can be obtained.
  • the material of the piercer plug according to the present invention has a hardness of HRC6 to 40 and is characterized by having a content of diffusible hydrogen limited to 2 ppm or less and by having a structure which comprises mainly tempered martensite and/or bainite. These characteristics are built by the heat treatment conditions after casting the component materials forming the piercer plug.
  • the method of manufacturing the material for piercer plug according to the present invention as shown in FIG. 1 , first smelts steel having the above predetermined composition, then casts the steel at a casting step S1 to obtain material for piercer plug. After that, at the heat treatment step S2, it performs heat treatment for adjusting the hardness and dehydrogenating the material for piercer plug.
  • the heat treatment step S2 comprises heating the material for piercer plug to be heat treated up to a predetermined heat treatment temperature, holding the material for piercer plug at the heat treatment temperature for a predetermined time, and cooling the material for piercer plug after the elapse of the predetermined time.
  • the heat treatment conditions will be explained from the viewpoint of the hardness of the material for piercer plug and the viewpoint of the concentration of diffusible hydrogen. Note that, in the present invention, the heat treatment temperature indicates the surface temperature of the material for piercer plug.
  • the Steel Nos. 1 to 18 of the compositions which are described in Table 1 were subject to high frequency melting and cast into molds for piercer plug (size: 160 ⁇ 400L).
  • the cast steels were heat treated under the Heat Treatment Conditions 1-1 to 8-3 which are described in Table 2 to obtain the Test Piece Nos. 1 to 37 which are shown in Table 3.
  • the results of measurement of the surface hardness (HRC) and the carbon equivalents and heat treatment parameters of the test piece are shown in Table 3.
  • the compositions of the test pieces correspond to the composition numbers of Table 1.
  • the inventors plotted the relationship between the carbon equivalents and heat treatment parameters described in Table 3 as shown in FIG. 2 and studied the relationship between hardness (HRC) and the carbon equivalent (C equivalent). Table 1 (mass%) Composition No.
  • Cooling Condition 2 Retaining material for piercer plug in furnace at retention temperature (°C) for retention time (Hr), then furnace cooling by 2°C/min average cooling rate down to 480°C, then taking out material for piercer plug from furnace and allowing the material to naturally cool in air.
  • Cooling Condition 3 Retaining material for piercer plug in furnace at retention temperature (°C) for retention time (Hr), then taking out material for piercer plug from furnace and allowing the material to naturally cool in air.
  • the heat treatment parameter (P H ) is defined as in the following formula 1.
  • the carbon equivalent (C equivalent) has a large effect on the hardness of the steel composition, so was used as an indicator.
  • the carbon equivalent is defined by the following formula 4.
  • FIG. 2 shows the relationship between the carbon equivalent (C equivalent) and the heat treatment parameter P H .
  • the numerical values which are attached near the white circles in FIG. 2 show the HRC values of the test pieces. From FIG. 2 , the inventors discovered that to adjust the hardness of the material for piercer plug to a suitable range of HRC6 to 40 in range, the heat treatment conditions should be set so that the heat treatment parameter P H satisfies the following formula 2 and formula 3.
  • P H T ⁇ 22 + log 10 ⁇ Hr P H ⁇ 7500 ⁇ C eq + 20900 ⁇ and P H ⁇ 27500 P H ⁇ 5000 ⁇ C eq + 14500 wherein, T indicates the heat treatment temperature in units of °K.
  • the heat treatment temperature T is the surface temperature of the material for piercer plug.
  • Hr indicates the retention time, that is, the time for retaining the material for piercer plug at the heat treatment temperature T in units of hours.
  • C eq indicates the carbon equivalent of the material for piercer plug and is defined by the following formula 4.
  • C eq C + Si / 4 + Mn / 6 + Cu + Ni / 15 + Cr / 5 + Mo / 5
  • C, Si, P, Al, and Mn are the contents of the elements (mass%).
  • test pieces which have C equivalents of 0.5 to 1.8 are given HR6 to 40 hardnesses by heat treatment conditions in the ranges of formula 2 which shows the upper limit of the heat treatment parameter P H and formula 3 which shows the lower limit. Further, if comparing a plurality of test pieces which have similar C equivalents, it will be understood that the HRC value becomes higher the lower the heat treatment parameter P H .
  • the hardness of the material for piercer plug after heat treatment is preferably HRC20 to 40.
  • a material for piercer plug which has such a preferable range of hardness can be manufactured by heat treating a material for piercer plug which has a composition in the range of the above C equivalent under heat treatment conditions which include a heat treatment parameter P H satisfying the following formula 5: P H ⁇ 5000 ⁇ C eq + 17500 ⁇ and P H ⁇ 25000
  • the heat treatment step is preferably completed within 24 hours including the temperature elevation and cooling from the viewpoint of productivity.
  • the thickness of the oxide scale which was formed on the surface of the material for piercer plug was usually 100 ⁇ m or so. It was confirmed that this extent of oxide scale can be easily removed by cutting, grinding, etc.
  • Heat treatment comprising retaining the material at 550°C to 900°C in temperature range for 0.5 hour to 10 hours can be used to reduce the content of diffusible hydrogen in the material for piercer plug.
  • the content of diffusible hydrogen of the material for piercer plug after casting is 7 ppm or more, but it was confirmed that if retaining the material at this temperature range for at least 0.5 hour, the content of diffusible hydrogen of the material for piercer plug becomes 2 ppm or less.
  • the heat treatment atmosphere may be the air.
  • the cooling after this heat treatment is the step which determines the structure of the material for piercer plug.
  • the structure of the material for piercer plug is suitably tempered martensite and/or bainite.
  • material for piercer plug with a carbon equivalent of 0.5 to 1.8 in range is cast, then left in as-cast state, as explained above, the structure becomes mainly tempered martensite. Therefore, to obtain toughness, a 550°C to 900°C heat treatment temperature is used for heat treatment.
  • the cooling after heat treatment also has the effect of causing the precipitated carbides to grow to a certain extent and become spheroidal. Furthermore, the state of precipitation of Mo and W appears in the hardness. That is, by suitable precipitation, the hardness can be suppressed.
  • the hardness of the material for piercer plug falls.
  • the Mo and W which form a solid solution in the material for piercer plug precipitate and the hardness falls.
  • the material for piercer plug is preferably cooled by a 5°C/min or less cooling rate down to a 480°C or less temperature.
  • the cooling rate is preferably a 1°C/min or less cooling rate.
  • the cooling rate is slow and gradual cooling.
  • the cooling rate is preferably 0.1°C/min or more.
  • Furnace cooling can be used for gradual cooling. For example, it is possible to cool down the furnace to 480°C or less, then take out the material for piercer plug from the furnace and allow it to cool in air. Alternatively, it is possible to cool down the furnace to room temperature, then take out the material for piercer plug from the furnace.
  • the natural cooling of the cooling condition 3 of Table 2 is performed from when the material for piercer plug becomes a temperature lower than 480°C, so does not affect the structure, precipitates, and hydrogen content of the material for piercer plug.
  • the material for piercer plug which is adjusted by the heat treatment step S2 to a HRC6 to 40 hardness is shaped by the shaping step S3 to a material for piercer plug for manufacturing seamless steel pipe which has a predetermined shape.
  • the shaping step S3 can be cut etc. Further, the shaping step S3 may be performed right after the heat treatment step S2 or may be performed after long term storage of the material for piercer plug since no season cracking occurs.
  • the material for piercer plug for manufacturing seamless steel pipe of the present invention can be shaped by the shaping step S3 to a predetermined tool shape, then a protective coating can be formed on its surface by various methods in a protective coating forming step S4.
  • a protective coating forming step S4 for example, it is possible to perform at least one type of heat treatment which forms a scale layer, treatment for coating a ceramic or other protective coating by thermal spraying, or other treatment.
  • the method in a protective coating forming step S4 is not particularly limited.
  • Test Piece No. 6 to No. 11 which are described in Table 3 were prepared as Examples 1 to 6 of the present invention which are shown in Table 4. Further, for comparison with the present invention, except for using Steel No. 1 and Steel No. 2 which were described in Table 1 and heat treating the Steel No. 1 and Steel No. 2 under the following Heat Treatment Condition A, the same manufacturing conditions as for the examples of Table 1 were used for manufacturing the materials for piercer plug of Comparative Examples 1 and 2.
  • Heat Treatment Condition A (Comparative Example): Natural Cooling in Air as-Cast state
  • H 2 analysis samples were stored immersed in liquid nitrogen right after being cut out from the materials for piercer plug.
  • the above H 2 analysis sample was taken out from liquid nitrogen and washed by ultrasonic washing. After that, the H 2 analysis sample was dried by cold air, weighed, and used for various measurements.
  • the diffusible hydrogen which is contained in the H 2 analysis sample was measured by inserting the H 2 analysis sample in a mass spectrometry apparatus, exhausting the air for 10 minutes, then heating in a vacuum with an initial pressure at the start of measurement of about 1.4 ⁇ 10 -5 Pa by a 100°C/hour (1.67°C/min) constant rate of temperature rise from room temperature to 600°C and analyzing the mass spectral intensity of hydrogen which arises at the time of heating. Further, the mass spectral intensity of hydrogen was analyzed by using a mass spectrometer (made by Canon-Anelva, quadrapole mass spectrometer M201QA-TDM).
  • Examples 1 to 6 that is, materials for piercer plug of the Heat Treatment Conditions 3-1, 3-2, and 6-3 according to the present invention, did not suffer from any season cracking at all regardless of the differences in compositions of the Steel 1 and the Steel 2 even if held for 30 days in air.
  • Comparative Examples 1 and 2 that is, materials of the Heat Treatment Condition A, suffered from season cracking from 14 days. After the elapse of 30 days, 16 samples (80%) were confirmed to suffer from season cracking. No season cracking was confirmed in the materials of Heat Treatment Conditions 3-1, 3-2, and 6-3. From the above, it was confirmed that season cracking was suppressed by the dehydrogenation effect according to the present invention.
  • the toughness was evaluated by a Charpy impact test at 20°C. Two each test pieces were prepared by being cut from the materials for piercer plug of Examples 1 to 6 and Comparative Examples 1 to 4 and were tested at room temperature (20°C) by a Charpy impact test. Further, for the test for evaluation of the toughness, the Test Piece No. 24 of Table 3 was used as the material for piercer plug of Example 7. The same technique as for Examples 1 to 6 and Comparative Examples 1 and 2 was used for the Charpy impact test of Example 7. The results of evaluation of toughness by the Charpy impact test are shown in Table 7. Under the Heat Treatment Conditions 3-1, 3-2, 6-1, and 6-3, the results were 17 to 70J/cm 2 in level.
  • each piercer plug Using as a model piercer (test-use piercer) each piercer plug, the following round billet heated to 1200°C was shaped by rotary piecing. Each plug was used for piercing-rolling five times, then the size of deformation of the tip of the plug from the initial shape was measured as the amount of deformation. The results are shown in Table 8.
  • Examples A1 to A4 have hardnesses in the range of the present invention, so the amount of deformation of the plug after five repeated piercing-rolling operations is small.
  • Comparative Examples B1 and B2 have hardnesses of less than HRC6, so the amount of deformation of the plug after five repeated piercing-rolling operations is a large one of about two times. Note that, if the amount of deformation is 1.5 mm or less, the plug can be recycled.
  • the present invention can be utilized as a material for a piercer plug for manufacturing seamless steel pipe. Further, the material for piercer plug according to the present invention can be stored for a long time and is easy to work into a suitable shape.

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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)
  • Heat Treatment Of Articles (AREA)
  • Moulds For Moulding Plastics Or The Like (AREA)
EP13842050.0A 2012-09-28 2013-09-26 Lochdornmaterial zur herstellung eines nahtlosen stahlrohrs und verfahren zur herstellung des materials Active EP2902522B1 (de)

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JP2012217720 2012-09-28
PCT/JP2013/076081 WO2014050975A1 (ja) 2012-09-28 2013-09-26 シームレス鋼管製造用ピアサープラグ用素材およびその製造方法

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EP2902522A1 true EP2902522A1 (de) 2015-08-05
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EP3498388A4 (de) * 2016-08-08 2019-06-19 Nippon Steel Corporation Verfahren zur herstellung eines durchstechsteckers
EP3822381A4 (de) * 2018-07-09 2022-01-26 Nippon Steel Corporation Nahtloses stahlrohr und herstellungsverfahren dafür

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JP6385195B2 (ja) * 2014-08-19 2018-09-05 新報国製鉄株式会社 シームレスパイプ製造用ピアサープラグ
CN106077097A (zh) * 2016-06-02 2016-11-09 天津钢管集团股份有限公司 提高穿孔机组顶头表面性能的结构及制作方法
CN111315906A (zh) * 2017-11-02 2020-06-19 日本制铁株式会社 穿轧机顶头及其制造方法
CN110616364B (zh) * 2018-06-20 2021-08-13 宝山钢铁股份有限公司 一种经济型无缝钢管高穿孔寿命顶头及其制造方法
CN112881121A (zh) * 2021-01-15 2021-06-01 常州宝菱重工机械有限公司 钢管穿孔顶头表面氧化膜评定方法
CN112899564A (zh) * 2021-01-15 2021-06-04 常州宝菱重工机械有限公司 钢管穿孔顶头及制备方法
CN117987746A (zh) * 2024-03-27 2024-05-07 南通市嘉业机械制造有限公司 一种耐磨无缝钢管穿孔顶头及其制备方法

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Publication number Priority date Publication date Assignee Title
CN105546228A (zh) * 2016-01-20 2016-05-04 浙江海洋学院 一种船舶用无缝钢管及其制备方法
EP3498388A4 (de) * 2016-08-08 2019-06-19 Nippon Steel Corporation Verfahren zur herstellung eines durchstechsteckers
EP3822381A4 (de) * 2018-07-09 2022-01-26 Nippon Steel Corporation Nahtloses stahlrohr und herstellungsverfahren dafür

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CN104685085A (zh) 2015-06-03
BR112015006482B8 (pt) 2020-10-13
WO2014050975A1 (ja) 2014-04-03
JPWO2014050975A1 (ja) 2016-08-22
TW201420777A (zh) 2014-06-01
BR112015006482B1 (pt) 2020-01-28
BR112015006482A2 (pt) 2017-07-04
CN104685085B (zh) 2016-10-26
EP2902522B1 (de) 2018-06-27
EP2902522A4 (de) 2016-06-15
TWI487800B (zh) 2015-06-11
JP6195570B2 (ja) 2017-09-13

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