CN1788101A - Tool steel for hot working, tool for hot working and plug for producing seamless pipe - Google Patents
Tool steel for hot working, tool for hot working and plug for producing seamless pipe Download PDFInfo
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- CN1788101A CN1788101A CN 200480013137 CN200480013137A CN1788101A CN 1788101 A CN1788101 A CN 1788101A CN 200480013137 CN200480013137 CN 200480013137 CN 200480013137 A CN200480013137 A CN 200480013137A CN 1788101 A CN1788101 A CN 1788101A
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- oxide skin
- perforation
- hot working
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- 229910001315 Tool steel Inorganic materials 0.000 title claims abstract description 18
- 229910052761 rare earth metal Inorganic materials 0.000 claims abstract description 17
- 238000004519 manufacturing process Methods 0.000 claims abstract description 15
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 13
- 229910052802 copper Inorganic materials 0.000 claims abstract description 10
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 10
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 8
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 7
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 6
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 6
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 5
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 5
- 229910052796 boron Inorganic materials 0.000 claims abstract description 4
- 238000010438 heat treatment Methods 0.000 claims description 15
- 239000012535 impurity Substances 0.000 claims description 12
- 229910052747 lanthanoid Inorganic materials 0.000 claims description 4
- 150000002602 lanthanoids Chemical class 0.000 claims description 4
- 229910052706 scandium Inorganic materials 0.000 claims description 4
- 229910052727 yttrium Inorganic materials 0.000 claims description 4
- 229910000831 Steel Inorganic materials 0.000 abstract description 90
- 239000010959 steel Substances 0.000 abstract description 90
- 229910052804 chromium Inorganic materials 0.000 abstract description 4
- 230000003647 oxidation Effects 0.000 description 25
- 238000007254 oxidation reaction Methods 0.000 description 25
- 229910052751 metal Inorganic materials 0.000 description 23
- 239000002184 metal Substances 0.000 description 23
- 230000000694 effects Effects 0.000 description 19
- 239000011159 matrix material Substances 0.000 description 19
- 239000000463 material Substances 0.000 description 17
- 150000001875 compounds Chemical class 0.000 description 16
- 238000005096 rolling process Methods 0.000 description 13
- 238000003490 calendering Methods 0.000 description 12
- 238000002844 melting Methods 0.000 description 12
- 230000008018 melting Effects 0.000 description 11
- 239000010935 stainless steel Substances 0.000 description 11
- 229910001220 stainless steel Inorganic materials 0.000 description 11
- 229910052596 spinel Inorganic materials 0.000 description 10
- 239000011029 spinel Substances 0.000 description 10
- 208000037656 Respiratory Sounds Diseases 0.000 description 9
- 238000000034 method Methods 0.000 description 9
- 238000007669 thermal treatment Methods 0.000 description 9
- 229910000851 Alloy steel Inorganic materials 0.000 description 8
- 239000000853 adhesive Substances 0.000 description 8
- 230000001070 adhesive effect Effects 0.000 description 8
- 239000000203 mixture Substances 0.000 description 8
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 8
- 229910045601 alloy Inorganic materials 0.000 description 7
- 239000000956 alloy Substances 0.000 description 7
- 238000001816 cooling Methods 0.000 description 7
- 230000009466 transformation Effects 0.000 description 7
- 230000015572 biosynthetic process Effects 0.000 description 6
- 230000033228 biological regulation Effects 0.000 description 5
- 239000000470 constituent Substances 0.000 description 4
- 239000002826 coolant Substances 0.000 description 4
- 230000004927 fusion Effects 0.000 description 4
- 238000009413 insulation Methods 0.000 description 3
- 239000002994 raw material Substances 0.000 description 3
- 230000000630 rising effect Effects 0.000 description 3
- 239000007858 starting material Substances 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 229910004283 SiO 4 Inorganic materials 0.000 description 2
- 230000015556 catabolic process Effects 0.000 description 2
- 239000002131 composite material Substances 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 238000006731 degradation reaction Methods 0.000 description 2
- 229910052840 fayalite Inorganic materials 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 229910052760 oxygen Inorganic materials 0.000 description 2
- 206010013786 Dry skin Diseases 0.000 description 1
- 229910018054 Ni-Cu Inorganic materials 0.000 description 1
- 229910018481 Ni—Cu Inorganic materials 0.000 description 1
- 239000003570 air Substances 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 239000001273 butane Substances 0.000 description 1
- 229910002091 carbon monoxide Inorganic materials 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 125000003636 chemical group Chemical group 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 238000002485 combustion reaction Methods 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000000280 densification Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000005496 eutectics Effects 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 239000000314 lubricant Substances 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- IJDNQMDRQITEOD-UHFFFAOYSA-N n-butane Chemical compound CCCC IJDNQMDRQITEOD-UHFFFAOYSA-N 0.000 description 1
- OFBQJSOFQDEBGM-UHFFFAOYSA-N n-pentane Natural products CCCCC OFBQJSOFQDEBGM-UHFFFAOYSA-N 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 230000000704 physical effect Effects 0.000 description 1
- 238000004064 recycling Methods 0.000 description 1
- 238000010079 rubber tapping Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 230000035945 sensitivity Effects 0.000 description 1
- 238000005507 spraying Methods 0.000 description 1
- 239000003381 stabilizer Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
Classifications
-
- 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
-
- 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
- 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
- C22C38/18—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
- 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
- C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Articles (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
本发明为一种热加工用工具钢，在其表面生成的氧化皮的粘附性与润滑性良好，强度高。该工具钢含有C：0.05～0.5％，Si：0.1～1％，Mn：1.6～3.5％，Ni：0.05～0.5％，Mo：2～5％，W：2～5％，Cu：0.05～0.5％，剩余部分实质上由Fe所构成。还可以含Cr、Co、REM、Ti、Nb、V、Zr及B中的1种以上。由该钢制作的工具，其表面由厚度为50～1500μm的氧化皮覆盖。工具的代表例为无缝管制造用的穿孔顶头。The present invention is a tool steel for hot working, and the oxide scale formed on the surface thereof has good adhesion and lubricity and high strength. The tool steel contains C: 0.05-0.5%, Si: 0.1-1%, Mn: 1.6-3.5%, Ni: 0.05-0.5%, Mo: 2-5%, W: 2-5%, Cu: 0.05- 0.5%, and the remainder is substantially composed of Fe. One or more of Cr, Co, REM, Ti, Nb, V, Zr, and B may also be contained. The surface of a tool made of this steel is covered with an oxide scale with a thickness of 50 to 1500 μm. A typical example of the tool is a piercing plug for seamless pipe production.
Description
Technical field
The present invention relates to a kind of tool for thermal processing steel and tool for thermal processing.Tool steel of the present invention is suitable as the starting material of the top of the perforation rolling press (for example, mannesmann piercer) that uses in the manufacturing of the seamless tube that comprises high Cr steel alloy and Ni base alloy.So-called high Cr steel alloy is to be the steel of representative with the stainless steel that contains the Cr more than 13%.
Background technology
At present, be used to make the rolling press of weldless steel tube, wherein be the top that the perforation rolling press of representative is used, do that its top is used after implementing the thermal treatment that forms oxide skin on the surface by the steel that basic composition is surplus Fe of 3%Cr-1%Ni-with the mannesmann piercer.This top is perforation usefulness when making weldless steel tube with ordinary steel.
But, to by the stainless steel that contains the Cr more than 13% being seamless tube that the high Cr steel alloy of representative and Ni base alloy is made when boring a hole calendering, because the temperature on surface, top and surface pressure rise, so the life-span of top obviously shortens.For example, in the perforation of the SUS304 of JIS material, 1 pass top just deforms.
In perforation calendering, to the cooling of spraying water of the king roller of perforation rolling press.This water coolant scatters to pyritous top, firm perforation back.Therefore, the surface of top is cooled suddenly, and part takes place the oxide skin on surface peels off, and this released part becomes the reason that burn-back takes place when boring a hole calendering next time.Also have, use in order to prepare next time, the top after will using usually is immersed in the water coolant cools off, but the cooling of this moment makes the feed metal of top produce the phase transformation crackle sometimes.
There is following motion the top that the perforation rolling press that uses during as the manufacturing that with the stainless steel that contains the Cr more than 13% is the seamless tube made of the high Cr steel alloy of representative and Ni base alloy etc. is used.
(a) improve anti-burn-back by reducing Cr content, added the top (Japanese documentation 1) that adhering steel that Mo and W etc. have improved hot strength and oxide skin is made.
(b) by having improved the oilness of oxide skin, anti-separability and wear resistant by heavy addition Ni, and, by adding excessive Mo or/and W has improved the top (Japanese documentation 2) that the steel of hot strength is made.
(c), and limit matrix metal and oxide skin rough interface degree, the top (Japanese documentation 3) of having improved anti-burn-back and oilness by by making with the same steel in the top of above-mentioned (b).
(d) except Ni, Cr, Co, W or/and the Mo, also contain the top with excellent in resistance abradability (Japanese documentation 4) that Cu makes as steel that must composition.
(e) except Cr, Ni, Co, Cu, W or/and Mo, the top (Japanese documentation 5) of the anti-fragility of rapid heat cycle when recycling of also having contained raising that Ti or Zr make as steel that must composition.
[patent documentation 1] Japanese Patent spy opens clear 63-282241 communique
[patent documentation 2] Japanese patent laid-open 4-74848 communique
[patent documentation 3] Japanese patent laid-open 4-270003 communique
[patent documentation 4] Japanese Patent spy opens clear 57-152446 communique
[patent documentation 5] Japanese Patent spy opens clear 60-208458 communique
But, top (a), the hot strength of matrix metal and the adhesivity of oxide skin are not enough, to the perforated steel billit of long size the time, promptly can not guarantee enough life-spans when the long perforation calendering of the length of boring a hole.
(a) to the top of (c), oxide skin fusion in perforation procedure of the leading section of the top that surface pressure maximum, temperature raise, lost insulation effect and wear resistant, melting loss and distortion take place in the front end of top easily.
(d) to the top of (e),, and, exist the front end that comes directly towards that the shortcoming of melting loss and distortion takes place easily because hot strength is also not enough owing to the not only anti-burn-back variation of too high levels of Cr.
Summary of the invention
Even first purpose of the present invention provides and a kind ofly uses, also has the tool steel of longer life and with the instrument of this kind steel manufacturing when the big material of thermal processing distortion resistance.
Second purpose of the present invention provides a kind of perforation rolling press when making seamless tube by the material that with the stainless steel that contains 13% above Cr is the high Cr steel alloy of representative and Ni base alloy one class with the top, and this head lifetime is long and be not easy to take place burn-back.
Present inventors have carried out all research in order to finish above-mentioned problem, obtain following opinion.
(a) when being high Cr steel alloy tubulation more than 13% with Cr content, the physical properties of the oxide skin that the surface, top forms and material thereof are that the intensity of tool for thermal processing steel (below, be called " heading material ") had a significant impact life-span of top.
(b) material of the top used of present employed stainless steel tubulation contains promising raising hot strength and the Cr that adds.But because the avidity height of Cr and oxygen, with the top that the material that contains Cr is made, if prevent the thermal treatment of the formation oxide skin of burn-back, the matrix metal side of oxide skin forms the spissated spinel type squama of Cr oxide compound,, contains lot of F e that is
2CrO
4Internal layer squama layer.This spinel type squama is about 20～90 quality % that reach the internal layer squama.
The Cr concentration of matrix metal is high more, and the concentrated ratio of the Cr in the internal layer squama also uprises.For example when the Cr that contains 0.5% in the matrix metal, the Cr concentration in the internal layer squama is about 1～5%.
(c) generally when machined material and instrument contain composition of the same race, burn-back takes place easily.Because stainless steel contains Cr, so to its perforation calendering the time, the high more easy more generation burn-back of the concentrating degree of the Cr in the internal layer squama layer of top.So,, need to suppress the rising of the Cr concentration in the internal layer squama in order to prevent burn-back.
Based on above-mentioned opinion, can think that with the steel that does not contain Cr be a method that prevents burn-back as heading material.But the Cr in heading material is structure stability, the hot strength that improves the matrix metal of top, improves the adhesivity of the oxide skin that forms and the useful component that improves wear resistant.So in the prior art, it is the comparison difficulty that heading material uses the steel that does not add Cr.
Here, present inventors further investigate for the top of using as the stainless steel tubulation of the strengthening element of heading material without Cr, and the result has distinguished following situation.
(d) present, Mn is the element that is used for improving structure stability.But, by with the combination of other alloying constituents, as described below, have extremely effective function as the raw-material constituent of the top of carrying out the stainless steel perforation.
Mn and Cr are same, are austenite stabilizer element, make to be organized in high temperatures, improve hot strength simultaneously.In addition,, form the spinel type squama that contains the Mn oxide compound, that is, form and contain lot of F e in the matrix metal side of the oxide skin that forms by the thermal treatment that forms oxide skin if in the starting material of top, add a large amount of Mn
2MnO
4The internal layer squama.This Fe
2MnO
4About 20～90 quality % for the internal layer squama.
Contain the spinel type squama (Fe that contains above-mentioned Mn oxide compound in a large number
2MnO
4) the internal layer squama owing to contain Cr in fact or not, or diluted by Mn containing under the situation of Cr, and improve anti-burn-back when carrying out the stainless steel perforation significantly.On the other hand, along with concentrating of Mn, the wear resistant of internal layer squama improves, and the wearing and tearing of the oxidation cortex in the perforation reduce, and the life-span of top improves.
(e) Mn is different with Cr, is not the element that suppresses steel oxidation.So, not containing in the top of steel of Mn will not containing Cr as material, the thermal treatment of formation oxide skin that can be by the following short period of time of low temperature forms the oxidation cortex of adequate thickness.In addition, compare with the heading material that contains Cr of prior art owing to be easy to oxidation, so, also form oxide skin on the surface of top easily, and improve owing to the existence of this oxide skin the life-span of top even during the cooling after perforation procedure finishes.
(f) still, if add Mn too much, the crack sensitivity of steel obviously increases, and when water coolant etc. scattered to the surface, top of just having used in the perforation calendering, the surface, top can produce the crack sometimes.So its addition is limited.In addition, need W and the Mo of compound interpolation as the element that improves hot strength.
(g) fusing point that contains the internal layer squama of Mn oxide compound is more than 1200 ℃, not fusion in the perforation procedure.Therefore, do not show lubricant effect, the time that perforation needs is long, and the surface temperature of top rises, and melting loss.So, have oilness in order to make oxide skin, need to optimize the fusing point of oxide skin.In order to optimize this fusing point, can utilize W oxide compound and Fe oxide compound near 1100 ℃, eutectic reaction to take place, and near the fact of the fusing point of the composite oxides of Fe and Si 1170 ℃.That is, if suitably adjust the content of W and Si, the formation of W oxide compound in can the promotes oxidn skin and the composite oxides of Fe and Si can be optimized the fusing point of oxide skin.
(h) contain the spinel type squama (Fe that contains above-mentioned Mn oxide compound in a large number
2MnO
4) the internal layer squama, promptly contain lot of F e with the spissated spinel type squama of Cr oxide compound
2CrO
4The internal layer squama sticking power of comparing low, burn-back and melting loss take place owing to peeling off in oxidation cortex easily in the tubulation process.
(i) yet, if be the metallics that is scattered in its layer with the internal layer squama, the energy of deformation of oxide skin increases, adhesive power improves, oxide skin not taking place in perforation peel off, and heating under the refrigerative environment peeling off of inhibited oxidation skin significantly repeatedly, improves oilness and wear resistance yet.
(j), can enumerate Ni, Cu and Co particle as above-mentioned metallics.Because these metallicss, even to the steel that contains them being raw-material top when forming the thermal treatment of oxide skin, can be not oxidized yet, so metallics directly disperses to separate out in the oxidation cortex.
(k) still, excessive interpolation Ni rises the martensitic transformation temperature of matrix metal.So, when making top cooling suddenly, cause the phase transformation crackle sometimes by the scattering of roll water coolant etc., cause the top damage.So the content of Ni is limited.But if reduce the content of Ni, adhesive power that mutually should the partial oxidation skin descends.
In addition,, just do not add Ni, then cause the Cu embrittlement, surface, damage top at the low-melting Cu metal level of the formation at the interface of oxide skin and matrix metal if only add Cu.But if an amount of Ni is added with Cu, being dispersed in the metallics in the oxide skin and the metal level of formation at the interface of oxide skin and matrix metal is the Ni-Cu alloy, can suppress above-mentioned Cu embrittlement.Not only like this, can also improve the spinel type squama that contains the Mn oxide compound, just Fe
2MnO
4Adhesivity to matrix metal.
(1) the raising effect of the adhesive power of Co oxide skin is lower than Ni, for the adhesive power that improves oxide skin by interpolation Co needs excessive interpolation.And excessive interpolation Co can cause the rising of the prices of raw and semifnished materials.So as heading material, the compound interpolation steel of preferred Ni and Cu also can add Co as required.
According to the present invention that above-mentioned many opinions are finished, mainly be the tool for thermal processing steel of following (1), the tool for thermal processing of following (2), and the top used of the perforation rolling press that uses in the manufacturing of the seamless tube manufacturing of following (3).In following record, be quality % about the % of component content.
(1) C:0.05～0.5%, Si:0.1～1%, Mn:1.6～3.5%, Ni:0.05～0.5%, Mo:2～5%, W:2～5%, Cu:0.05～0.5%, remainder: the tool for thermal processing steel that constitutes by Fe and impurity.
(2) made by above-mentioned (1) described tool for thermal processing steel, the thickness that its surface is formed by the thermal treatment that forms oxide skin is the tool for thermal processing that the oxide skin of 50～1500 μ m covers.
(3) made by above-mentioned (1) described tool for thermal processing steel, the thickness that its surface is formed by the thermal treatment that forms oxide skin is the top that the employed perforation rolling press of manufacturing of the seamless tube that covers of the oxide skin of 50～1500 μ m is used.
The tool for thermal processing steel of above-mentioned (1) except that mentioned component, can also contain at least a kind of composition at least 1 group that is selected among following (A)～(D) group.
(A)Cr：0.05～1％，
(B)Co：0.05～5％，
(C) more than 1 of Ti, Nb, V, Zr and B kind: add up to 0.05～0.5%,
(D)REM：0.001～0.2％。
REM is meant and contains from 15 elements of group of the lanthanides of La to Lu and totally 17 elements of Sc and Y.
Embodiment
Below, be elaborated for the reason that the employed tapping machine of manufacturing of tool for thermal processing steel of the present invention, tool for thermal processing and seamless tube is made as above-mentioned regulation of the top.
1. tool for thermal processing steel
C：0.05～0.5％
C is effective to the hot strength that improves steel.But, just can not get enough hot strengths if contain quantity not sufficient 0.05%.On the other hand, if it is too high to surpass 0.5% hardness as the hard-faced part after the instrument use, is easy to generate and hardening cracks.Therefore, the content of C is 0.05～0.5%.Lower limit is preferably 0.07%, and more preferably 0.1%.In addition, the upper limit is preferably 0.3%, and more preferably 0.2%.
Si：0.1～1％
Si is effective as the reductor of steel.In addition, not only at Ac
1The densification aspect of the oxide skin that the rising of transformation temperature and surface generate is effective, can also make to generate fayalite (Fe
2SiO
4) the high temperature deformation of oxide skin can increase, improve adhesivity.Can not get these effects if contain 0.1% of quantity not sufficient.On the other hand, if surpass 1% fayalite (Fe
2SiO
4) generate surplus, not only the fusing point of oxide skin descends, and hot hardness also descends.Based on these reasons, the content of Si is advisable 0.1～1%.Be preferably 0.15% as lower limit, more preferably 0.2%.In addition, be preferably 0.6%, more preferably 0.5% as the upper limit.
Mn：1.6～3.5％
For the form of the oxide skin that the surface generated of controlling steel, and the hot strength that improves steel, Mn is one of most important element to steel of the present invention.If contain the adhering effect of improving that quantity not sufficient 1.6% not only be can't see oxide skin, the raising effect of hot strength is also little, when using as instrument, can't see the raising in life-span.On the other hand, if surpass 3.5%, the anti-fragility of matrix metal descends, and the surface cracks lifetime during as the cooling after the instrument use.Because these reasons, suitable Mn content is 1.6～3.5%.Be preferably 2% as lower limit, more preferably 2.5%.In addition, be preferably 3.25%, more preferably 3.2% as the upper limit.
Ni：0.05～0.5％
Ni is especially containing Fe in a large number in the oxidation cortex
2MnO
4Internal layer squama layer in disperse to separate out as metallics, effective to the anti-separability that improves oxide skin.This effect is remarkable especially when adding with Cu described later.But, can not get above-mentioned effect if contain 0.05% of quantity not sufficient.On the other hand, if surpass 0.5%, anti-hardening cracking property of the phase transformation decline of steel.Therefore, Ni content is advisable 0.05～0.5%.Be preferably 0.15% as lower limit, more preferably 0.2%.In addition, be preferably 0.45%, more preferably 0.4% as the upper limit.
Mo：2～5％
Mo is not only effective to the hot strength that improves steel, still by with the compound interpolation of Ni and Cu to improve the adhering effective constituent of oxide skin.With can obtaining these effects more than 2%, but 5% its result is just saturated.So suitable Mo content is 2～5%.Be preferably 2.25% as lower limit, more preferably 2.5%.In addition, be preferably 4.5%, more preferably 4% as the upper limit.
W：2～5％
W can improve the hot strength of steel.Or the extremely important element of the oilness of controlled oxidation skin.So, need content to be at least 2%.On the other hand, if surpass 5%, the fusing point of oxide skin is crossed in low the use oxidation cortex and is peeled off easily, and burn-back takes place.Therefore, the suitable content of W is 2～5%.Be preferably 2.5% as lower limit, more preferably 3%.In addition, be preferably 4.5%, more preferably 4% as the upper limit.
Cu：0.05～0.5％
Cu at aspects such as adhesivity that improves oxide skin and oilnesies, is one of most important element with above-mentioned Ni in steel of the present invention simultaneously.As previously mentioned particularly by improving the adhesivity of oxide skin and oilness etc. significantly with the compound interpolation of Ni.
Cu can improve the adhering fact of oxide skin, by the cited Japanese documentation 4 in front and Japanese documentation 5 as can be known.But disclosed steel in these documents all is that Mn is at the steel below 1.5%.In addition, patent documentation 5 disclosed steel, the content of Cr is up to 1～3%.In contrast, in the steel of the present invention, Mn is 1.6～3.5%, even and the content of Cr under the situation of adding, also only be 0.05～0.5%.
In the steel that has increased Mn content, form the spinel type squama (Fe that contains the Mn oxide compound in a large number as mentioned above
2MnO
4) the internal layer squama.This squama has the aforesaid burn-back effect that prevents significantly, but compares poor adhesion with the squama that Cr has concentrated.Cu plays and improves its adhering effect.But, can not get this effect if contain 0.05% of quantity not sufficient.On the other hand, if surpass 0.5%, oxide skin and matrix metal generate the high soft alloy layer of Cu content at the interface, the anti-peeling force of oxide skin descends, oxide skin is brought to the machined material side from matrix metal in the operation of boring a hole, and burn-back takes place easily.Based on these reasons, the optimum range of Cu content is 0.05～0.5%.Be preferably 0.07% as lower limit, more preferably 0.075%.In addition, be preferably 0.4%, more preferably 0.3% as the upper limit.
It more than is the necessary composition of tool steel of the present invention.One of tool steel of the present invention, except that mentioned component, all the other are made of Fe and impurity.
Another tool steel of the present invention except that mentioned component, contains at least a composition that is selected from the following stated composition, and surplus portion is made of Fe and impurity.
Cr：0.05～0.5％
Though Cr can not add yet, because it is the effective element that makes the adhesivity raising of oxide skin, so can add as required yet.But can not get above-mentioned effect if contain 0.05% of quantity not sufficient.On the other hand, hardening crack easily if surpass 0.5%.In addition, as mentioned above,, add at stainless steel burn-back takes place man-hour easily if Cr content generates the spinel type squama that Cr has concentrated at most.Based on these reasons, the content of Cr is 0.05～0.5% for good when adding.
Co：0.05～5％
Though Co can not add yet, also identical simultaneously because it is to improve the flexible effective element with above-mentioned Ni, in the oxidation cortex, disperses to separate out as metallics, be the effective element of the anti-separability etc. of raising oxide skin.So also can add as required.But, can not get above-mentioned effect if contain 0.05% of quantity not sufficient.On the other hand, if surpass 5% metallics burn-back takes place easily too much, the thermal fatigue characteristics of instrument descends simultaneously, and instrument is when heating is with cooling repeatedly, chaps easily because of thermal fatigue in its surface.In addition, the formation of Guo Sheng Co inhibited oxidation skin.Therefore, the content of Co is 0.05～5% for good when adding.
Ti, Nb, V, Zr, B: each or the total more than 2 kinds, 0.05～0.5%
Though these elements can not add yet,, be to improve the flexible effective element, so can add as required more than a kind or 2 kinds because these elements all have the grain refined effect.But each or the content that adds up to can not get above-mentioned effect as if 0.05% of less than.On the other hand, the strength degradation of matrix metal the embrittlement phase appears, if surpass 0.5%.Therefore, the content of these elements when adding, each or the total more than 2 kinds are good with 0.05～0.5%.
REM：0.001～0.2％
REM (promptly comprising) from group of the lanthanides 15 elements of La to Lu and 17 elements of Sc and Y, though can not add yet, because these elements all are the adhering effective constituent of improving oxide skin, so also can add as required more than a kind.But, if each or 0.001% of the quantity not sufficient that contains that adds up to can not get above-mentioned effect, if surpass 0.2% embrittlement phase, strength degradation appear.Therefore, the content during interpolation, each or add up to 0.001～0.2% for good more than 2 kinds.
The rest part of tool for thermal processing steel of the present invention is Fe and impurity.As the P of impurity and the content of S, so long as the common level that contains as impurity in this kind steel does not then have special problem.But, because P and S make the adhesivity of oxide skin descend sometimes, so preferably the two all is controlled at below 0.01%.
2. tool for thermal processing steel and perforation rolling press are with the thickness of oxide skin of top
The perforation rolling press that is used for tool for thermal processing and seamless tube manufacturing of the present invention is made by the tool for thermal processing steel with above-mentioned chemical ingredients with the top.And it is the oxidation cortex covering of 50～1500 μ m that the thickness that is formed by " forming the thermal treatment of oxide skin " need be used in its surface.It is the reasons are as follows.
If the thickness less than 50 μ m of oxidation cortex, not only insulation effect is insufficient, and the temperature that can not suppress matrix metal fully rises, and the attrition of oxidation cortex is fast, and tool shape is distortion ahead of time, and oilness disappears simultaneously, thereby burn-back takes place.
On the other hand, if the thickness of oxidation cortex surpasses 1500 μ m, can form the many squama layers of space and micro-flaw, descend with the adhesive power of matrix metal, not only the squama layer is peeled off easily in the processing before use, and the splitting of ectonexine squama in use also takes place easily, cracks in product.It when this crackle is bored a hole in the top crackle of the pipe inner face after the perforation.So the suitable thickness of oxidation cortex is 50～1500 μ m.
The thickness of oxidation cortex is to have added up to the internal layer squama and the two thickness of the outer squama that forms thereon.Outer squama is with FeO and Fe
3O
4Be main body, its outermost layer is Fe
2O
3
3. tool for thermal processing steel, tool for thermal processing and the perforation rolling press manufacturing of top
Tool for thermal processing steel of the present invention, by by known operation meltings such as atmosphere scorification, AOD method and VOD methods, the molten steel that obtains is made steel ingot or steel billet with ingot casting method and Continuous casting process, then, as required by implementing the steel disc manufacturing that hot calender etc. is thermally processed into the defined shape.Creating conditions of this moment has no particular limits.
The top that the perforation rolling press of tool for thermal processing steel of the present invention and seamless tube manufacturing usefulness is used, can by will be as above the molten steel direct pouring of gained become the instrument of regulation or the shape of top, or make with the instrument that forms regulation or the shape of top by steel billet being implemented heat forged.Creating conditions of this moment also has no particular limits.Just, form the thermal treatment of oxide skin, preferably under following condition, carry out.
4. form the heat treated condition of oxide skin
(1) heating atmosphere
Form in the processing of oxide skin, containing water vapor is very important in heating atmosphere, and the water vapor concentration in the stove need keep more than the 5 volume %.This condition can obtain by making the burning of fuel such as LNG, LPG, C gas and butane and air mixed.
(2) Heating temperature
The thickness of squama depends on Heating temperature and heat-up time.For the spinel type squama that contains the Mn oxide compound is in a large number formed with homogeneous thickness, preferably handling more than 800 ℃.In addition, if surpass 1200 ℃, the squama fusion of generation is so preferred Heating temperature is below 1200 ℃.
(3) heat-up time
Can determine according to Heating temperature heat-up time, to obtain the squama thickness of defined.
Embodiment
60 kinds of steel alloys with the chemical constitution shown in table 1 and the table 2 by atmosphere fusion melting, and after the steel ingot that obtains carried out heat forged, are cut outward, are shaped to the top that the perforation rolling press of seamless tube manufacturing usefulness is used.
The top of regulation shape will be shaped to, at LNG combustion atmosphere (volume %, 10%CO
2, 2%O
2, 20%H
2O, all the other: N
2) in, press all temperature and time heating of expression in table 3 and the table 4, and form the oxidation cortex of same all thickness of in table 3 and table 4, representing.
Use the resulting calendering of boring a hole that respectively comes directly towards.Perforation calendering is that the round steel billet perforation calendaring molding with the SUS304 system of following size is the hollow bloom of following size.The top is supplied with the perforation of a plurality of steel billets continuously.The perforation condition is as follows.
The size of steel billet and hollow bloom:
Parallel perforation is used
Steel billet diameter 70mm * length 1000mm
Hollow bloom diameter 72mm * length 2200mm
The expander perforation is used
Steel billet diameter 65mm * length 1000mm
Hollow bloom diameter 93mm * length 2200mm
The Heating temperature of steel billet: 1200 ℃
Crossing angle: 15 °
Pitch angle: 10 °
The size of top:
Parallel perforation diameter 54mm
Expander perforation diameter 75mm
The meaning of above-mentioned " parallel perforation " is that the external diameter of pipe (hollow bloom) after diameter and the perforation of steel billet is basic identical, and the meaning of " expander perforation " is that the external diameter of pipe is bigger than the diameter of steel billet.
To access times (perforation calendering radical) of each top that can supply with perforation calendering with use after the surface appearance of top investigate.Peeling off or attrition of oxidation cortex by observing the top, crackle or burn-back that the top takes place, can the melting loss of top front end or deformation state carry out the judgement that use.
With the thickness of the result of investigation and the heat-treat condition that forms oxide skin, oxidation cortex, and the tensile strength (TS:N/mm of starting material steel 1000 ℃ the time
2) together, expression in table 3 and table 4.
By table 3 and table 4 as can be known, by the top (symbol 1～31) that tool steel of the present invention is made, can use (perforation calendering) more than 8 times, and use the rear surface situation also good, demonstrate excellent performance.
Oxide skin because the content of Cu is very few, so the adhesive power of oxide skin is low, has taken place and has peeled off melting loss in the top relative therewith, that symbol 32 and 33 steel are made in the perforation.On the other hand, by the top that the steel of symbol 34 is made, because the content of Cu is too much, the front end burn-back has taken place in the matrix metal distortion in the perforation under the oxide skin.
The top that the steel of symbol 35 is made, hot strength is not enough because the content of Mn is very few, and perforation has been rolled 3 front ends distortion has just been taken place.And the top that the steel of symbol 36 is made is too much owing to the content of Mn, and body has taken place to hardening crack during perforation.
By the top that the steel of symbol 37 is made,, bore a hole and 4 times the front end melting loss has just taken place owing to the very few poor adhesion that makes oxide skin of the content of Ni.And the top that the steel of symbol 38 is made is because the content of Ni is too much, taken place to hardening crack during water-cooled after perforation.
By the top that the steel of symbol 39 is made, hot strength is not enough because the content of Mo is very few, bores a hole 4 times the front end distortion just to have taken place.And the top of being made by the steel of symbol 40 is because too much anti-the hardening cracking property of phase transformation of content of Ni and Mo is poor, and boring a hole has just produced the phase transformation crackle 3 times.
By the top that the steel of symbol 41 is made, hot strength is not enough because the content of W is very few, bores a hole 3 times the front end distortion just to have taken place.And the top of being made by the steel of symbol 42 is because the content of W is too much, and oxide skin is softening in the perforation, bores a hole and 4 times melting loss has just taken place.
By the top that the steel of symbol 43 is made, hot strength is not enough because the content of C is very few, uses 4 front ends that distortion has just taken place.And the top of making by the steel of symbol 44 since the content of C too much during the water cooling after perforation body crack.
By the top that the steel of symbol 45 is made, adhesive power oxide skin is not enough because the content of Si is very few, bores a hole 3 times the front end burn-back just to have taken place.And by the top that the steel of symbol 46 is made, because the too much oxide skin of content of Si is softening in perforation, bores a hole and 4 times the front end distortion has just taken place.
The top of making by the steel of symbol 47 and since the content of Cr too much during the water-cooled after perforation body produced crackle.The top of making by the steel of symbol 48 and 49 and since the content of Co too much in perforation front end taken place damaged.
By the top that the steel of symbol 50～54 is made, because the content more than any among Ti, Nb, V, Zr and the B is too much, front end has taken place damaged in perforation.In addition, the top of making by the steel of symbol 55～58 since the REM amount too much in perforation front end taken place damaged.
The top of making by the steel of symbol 59 and 60, though the chemical group Chengdu of matrix metal is in the scope of the present invention's regulation, but the top of making by the former steel, so, use 2 front ends just to be out of shape because the thickness of oxidation cortex was to be as thin as 45 μ m almost not have insulation effect.And the top of making by the latter's steel, because the thickness of oxidation cortex is blocked up to 1600 μ m and porous and adhesive power is low, the oxidation cortex of leading section is peeled off the result who comes off ahead of time, uses 4 front ends with regard to melting loss.
Table 1
| Classification | Symbol | Chemical constitution (quality %, rest part: Fe and impurity) | |||||||||
| C | Si | Mn | Ni | Mo | W | Cu | Cr | Co | Other | ||
| Example of the present invention | 1 | 0.15 | 0.28 | 2.90 | 0.32 | 2.95 | 3.90 | 0.05 | - | - | - |
| 2 | 0.13 | 0.29 | 3.10 | 0.32 | 3.30 | 4.15 | 0.10 | - | - | - | |
| 3 | 0.15 | 0.30 | 2.85 | 0.25 | 3.00 | 3.60 | 0.30 | - | - | - | |
| 4 | 0.14 | 0.28 | 2.95 | 0.30 | 2.95 | 4.20 | 0.48 | - | - | - | |
| 5 | 0.06 | 0.29 | 1.75 | 0.20 | 2.85 | 4.12 | 0.20 | - | - | - | |
| 6 | 0.20 | 0.35 | 3.04 | 0.30 | 3.00 | 4.13 | 0.15 | - | - | - | |
| 7 | 0.30 | 0.25 | 3.20 | 0.07 | 2.87 | 3.89 | 0.30 | 0.10 | - | - | |
| 8 | 0.35 | 0.45 | 2.98 | 0.20 | 3.21 | 4.02 | 0.10 | 0.20 | - | - | |
| 9 | 0.36 | 0.32 | 3.25 | 0.45 | 3.11 | 3.98 | 0.12 | - | - | - | |
| 10 | 0.35 | 0.65 | 3.20 | 0.10 | 3.10 | 2.55 | 0.09 | - | 0.50 | - | |
| 11 | 0.10 | 0.85 | 3.45 | 0.23 | 3.30 | 3.00 | 0.12 | - | 0.30 | - | |
| 12 | 0.20 | 0.20 | 2.50 | 0.30 | 2.90 | 4.25 | 0.22 | - | 4.50 | - | |
| 13 | 0.25 | 0.55 | 2.22 | 0.25 | 2.40 | 3.55 | 0.33 | 0.40 | 3.50 | - | |
| 14 | 0.30 | 0.25 | 3.20 | 0.07 | 2.05 | 3.89 | 0.28 | - | - | Ti：0.30 | |
| 15 | 0.35 | 0.30 | 3.11 | 0.45 | 4.21 | 3.25 | 0.19 | - | - | Nb：0.40 | |
| 16 | 0.48 | 0.40 | 2.89 | 0.30 | 3.21 | 3.65 | 0.07 | - | - | V：0.10 | |
| 17 | 0.35 | 0.25 | 3.11 | 0.45 | 3.33 | 3.90 | 0.36 | - | - | Zr：0.45 | |
| 18 | 0.25 | 0.60 | 3.45 | 0.50 | 4.25 | 3.99 | 0.40 | - | - | B：0.20 | |
| 19 | 0.15 | 0.30 | 3.00 | 0.29 | 3.33 | 3.25 | 0.36 | - | - | Ti+Nb：0.36 | |
| 20 | 0.30 | 0.30 | 3.20 | 0.20 | 4.80 | 3.89 | 0.28 | 0.40 | - | V：0.10 | |
| 21 | 0.35 | 0.25 | 3.11 | 0.45 | 3.33 | 3.25 | 0.19 | 0.43 | - | Nb+B：0.23 | |
| 22 | 0.35 | 0.25 | 2.22 | 0.25 | 2.40 | 3.55 | 0.19 | - | 2.00 | Ti+V：0.35 | |
| 23 | 0.15 | 0.30 | 3.00 | 0.33 | 3.00 | 3.33 | 0.07 | - | 4.50 | Zr：0.25 | |
| 24 | 0.15 | 0.30 | 3.20 | 0.20 | 4.80 | 3.89 | 0.36 | 0.38 | 3.70 | Ti+V+Nb：0.35 | |
| 25 | 0.35 | 0.25 | 2.95 | 0.30 | 2.95 | 4.20 | 0.36 | - | - | REM：0.02 | |
| 26 | 0.25 | 0.95 | 3.10 | 0.45 | 3.33 | 3.25 | 0.40 | - | - | REM：0.01 | |
| 27 | 0.30 | 0.30 | 3.20 | 0.20 | 4.80 | 3.89 | 0.36 | - | - | REM：0.005 | |
| 28 | 0.30 | 0.30 | 2.50 | 0.30 | 3.09 | 3.55 | 0.19 | 0.49 | - | REM：0.10 | |
| 29 | 0.35 | 0.25 | 3.11 | 0.30 | 2.95 | 4.20 | 0.07 | - | 4.50 | REM：0.15 | |
| 30 | 0.15 | 0.30 | 3.00 | 0.20 | 4.80 | 3.89 | 0.07 | 0.10 | 0.09 | REM：0.13 | |
| 31 | 0.35 | 0.25 | 3.11 | 0.45 | 3.33 | 3.25 | 0.19 | 0.10 | 0.09 | Zr：0.25、REM：0.15 | |
</entry></row></tbody></tgroup></table></tables>
Table 3
| Classification | The steel symbol | H in the atmosphere 2O concentration (Vol.%) | Heating temperature (℃) | Heat-up time (h) | Tensile strength (N/mm under 1000 ℃ 2) | Scale thickness (μ m) | Head lifetime (root /) | The damage status of top |
| Example of the present invention | 1 | 20 | 1050 | 6 | 120 | 800 | 9 | Well |
| 2 | 20 | 1100 | 4 | 115 | 800 | 8 | Well | |
| 3 | 20 | 1050 | 6 | 120 | 800 | 8 | Well | |
| 4 | 20 | 1050 | 6 | 100 | 800 | 9 | Well | |
| 5 | 20 | 1050 | 6 | 105 | 800 | 8 | Well | |
| 6 | 20 | 1050 | 6 | 120 | 800 | 9 | Well | |
| 7 | 20 | 1050 | 6 | 115 | 800 | 10 | Well | |
| 8 | 20 | 1050 | 6 | 115 | 800 | 11 | Well | |
| 9 | 20 | 1050 | 6 | 120 | 800 | 10 | Well | |
| 10 | 20 | 1050 | 6 | 122 | 800 | 9 | Well | |
| 11 | 20 | 1050 | 6 | 124 | 800 | 10 | Well | |
| 12 | 20 | 1050 | 6 | 121 | 800 | 10 | Well | |
| 13 | 20 | 1100 | 6 | 118 | 1200 | 10 | Well | |
| 14 | 20 | 1050 | 6 | 110 | 800 | 10 | Well | |
| 15 | 20 | 1050 | 6 | 105 | 800 | 10 | Well | |
| 16 | 20 | 1050 | 6 | 104 | 800 | 10 | Well | |
| 17 | 20 | 1050 | 4 | 121 | 900 | 11 | Well | |
| 18 | 20 | 1050 | 6 | 110 | 800 | 10 | Well | |
| 19 | 20 | 1050 | 6 | 105 | 800 | 10 | Well | |
| 20 | 20 | 1050 | 6 | 104 | 800 | 10 | Well | |
| 21 | 20 | 1050 | 8 | 110 | 970 | 10 | Well | |
| 22 | 20 | 1050 | 6 | 112 | 800 | 10 | Well | |
| 23 | 20 | 1050 | 8 | 108 | 970 | 10 | Well | |
| 24 | 20 | 1050 | 6 | 120 | 800 | 10 | Well | |
| 25 | 20 | 1050 | 6 | 118 | 800 | 10 | Well | |
| 26 | 20 | 1050 | 6 | 121 | 800 | 10 | Well | |
| 27 | 20 | 1050 | 8 | 108 | 970 | 10 | Well | |
| 28 | 20 | 1000 | 6 | 111 | 900 | 10 | Well | |
| 29 | 20 | 1050 | 6 | 110 | 800 | 10 | Well | |
| 30 | 20 | 1050 | 6 | 105 | 800 | 10 | Well | |
| 31 | 20 | 1050 | 6 | 105 | 800 | 10 | Well |
</entry></row></tbody></tgroup></table></tables>
Utilizability on the industry
Tool steel for hot working of the present invention has excellent elevated temperature strength. In addition, high in the adhesiveness of its surperficial oxide skin that forms and parent metal by the heat treatment that forms oxide skin, and the steel high with respect to Cr content, its anti-burn-back and lubricity are excellent. So, the tool for thermal processing of the present invention that is covered by the oxide skin of the specific thickness of giving by the heat treatment that forms oxide skin on its surface, long service life not only, and can not produce at product the blemish such as burn-back crackle. Tool steel of the present invention be particularly suitable as by take Cr content as the stainless steel more than 13% as representative the high Cr-containing alloy steel or the manufacturing of the seamless pipe made of Ni base alloy in the raw material of top of employed perforation calender. The long service life of this top, and help to make the few seamless pipe of inner face crackle with the required instrument consumption figure of lower unit product.
Claims (7)
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP134012/2003 | 2003-05-13 | ||
| JP2003134012 | 2003-05-13 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1788101A true CN1788101A (en) | 2006-06-14 |
| CN100494448C CN100494448C (en) | 2009-06-03 |
Family
ID=33447142
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CNB2004800131375A Expired - Fee Related CN100494448C (en) | 2003-05-13 | 2004-05-12 | Tool steel for hot working, tools for hot working, and plugs for seamless pipe manufacturing |
Country Status (5)
| Country | Link |
|---|---|
| EP (1) | EP1632583B1 (en) |
| JP (1) | JP4264755B2 (en) |
| CN (1) | CN100494448C (en) |
| DE (1) | DE602004029357D1 (en) |
| WO (1) | WO2004101837A1 (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101942610A (en) * | 2010-08-05 | 2011-01-12 | 黄贞益 | Piercing plug for hot-rolled seamless steel pipe and processing technology thereof |
| CN101646505B (en) * | 2007-02-05 | 2013-05-22 | 新日铁住金株式会社 | Manufacturing method of plug used for piercing and rolling of metal raw material, method of manufacturing metal pipe and plug used for piercing and rolling of metal raw material |
| CN103627979A (en) * | 2013-11-12 | 2014-03-12 | 铜陵市肆得科技有限责任公司 | Large-sized pump bearing steel material and preparation method thereof |
| CN103741061A (en) * | 2013-12-19 | 2014-04-23 | 马鞍山市方圆材料工程有限公司 | Alloy steel material with high fracture toughness for rolls and preparation method thereof |
| CN105452512A (en) * | 2013-08-06 | 2016-03-30 | 新日铁住金株式会社 | Seamless steel pipe for line pipe, and method for producing same |
| CN105821343A (en) * | 2016-05-24 | 2016-08-03 | 江苏金基特钢有限公司 | Production method of special steel |
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|---|---|---|---|---|
| EP2008731B1 (en) * | 2006-03-28 | 2014-06-25 | Nippon Steel & Sumitomo Metal Corporation | Method for surface treatment of a mandrel bar |
| EP2476772A1 (en) * | 2011-01-13 | 2012-07-18 | Rovalma, S.A. | High thermal diffusivity and high wear resistance tool steel |
| JP5566417B2 (en) * | 2012-04-19 | 2014-08-06 | 新日鐵住金株式会社 | Manufacturing method of perforated plug |
| JP6195570B2 (en) * | 2012-09-28 | 2017-09-13 | 新報国製鉄株式会社 | Material for piercer plug for seamless steel pipe manufacturing and manufacturing method thereof |
| KR101939510B1 (en) * | 2014-09-10 | 2019-01-16 | 신닛테츠스미킨 카부시키카이샤 | Austenitic stainless steel sheet which is not susceptible to diffusion bonding |
| DE102015122975B3 (en) * | 2015-12-30 | 2017-03-23 | Wolfgang Dörr | Method for producing a hot forming tool |
| CN106191694B (en) * | 2016-07-05 | 2019-04-09 | 左其福 | It is hot-forged warm extrusion cold punching tool and mould dual-purpose steel |
| CN111315906A (en) * | 2017-11-02 | 2020-06-19 | 日本制铁株式会社 | Piercing-rolling machine plug and manufacturing method thereof |
Family Cites Families (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS58123859A (en) * | 1982-01-18 | 1983-07-23 | Daido Steel Co Ltd | Hot working tool steel |
| JP2940188B2 (en) * | 1991-02-23 | 1999-08-25 | 住友金属工業株式会社 | Hot pipe making tool and method for producing the same |
| JPH08193241A (en) * | 1994-09-26 | 1996-07-30 | Kawasaki Steel Corp | Hot working tool and its production |
| JPH08206709A (en) * | 1994-12-09 | 1996-08-13 | Sumitomo Metal Ind Ltd | Hot pipe making tool and its manufacturing method |
-
2004
- 2004-05-12 JP JP2005506176A patent/JP4264755B2/en not_active Expired - Fee Related
- 2004-05-12 WO PCT/JP2004/006373 patent/WO2004101837A1/en active Application Filing
- 2004-05-12 CN CNB2004800131375A patent/CN100494448C/en not_active Expired - Fee Related
- 2004-05-12 EP EP04732422A patent/EP1632583B1/en not_active Expired - Lifetime
- 2004-05-12 DE DE602004029357T patent/DE602004029357D1/en not_active Expired - Lifetime
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101646505B (en) * | 2007-02-05 | 2013-05-22 | 新日铁住金株式会社 | Manufacturing method of plug used for piercing and rolling of metal raw material, method of manufacturing metal pipe and plug used for piercing and rolling of metal raw material |
| CN101942610A (en) * | 2010-08-05 | 2011-01-12 | 黄贞益 | Piercing plug for hot-rolled seamless steel pipe and processing technology thereof |
| CN105452512A (en) * | 2013-08-06 | 2016-03-30 | 新日铁住金株式会社 | Seamless steel pipe for line pipe, and method for producing same |
| US9651175B2 (en) | 2013-08-06 | 2017-05-16 | Nippon Steel & Sumitomo Metal Corporation | Seamless steel pipe for line pipe |
| CN103627979A (en) * | 2013-11-12 | 2014-03-12 | 铜陵市肆得科技有限责任公司 | Large-sized pump bearing steel material and preparation method thereof |
| CN103741061A (en) * | 2013-12-19 | 2014-04-23 | 马鞍山市方圆材料工程有限公司 | Alloy steel material with high fracture toughness for rolls and preparation method thereof |
| CN103741061B (en) * | 2013-12-19 | 2016-01-27 | 马鞍山市方圆材料工程有限公司 | A kind of roll high-fracture toughness alloy steel material and preparation method thereof |
| CN105821343A (en) * | 2016-05-24 | 2016-08-03 | 江苏金基特钢有限公司 | Production method of special steel |
Also Published As
| Publication number | Publication date |
|---|---|
| CN100494448C (en) | 2009-06-03 |
| JP4264755B2 (en) | 2009-05-20 |
| JPWO2004101837A1 (en) | 2006-07-13 |
| EP1632583A1 (en) | 2006-03-08 |
| WO2004101837A1 (en) | 2004-11-25 |
| EP1632583B1 (en) | 2010-09-29 |
| EP1632583A4 (en) | 2006-06-28 |
| DE602004029357D1 (en) | 2010-11-11 |
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