JP2007107073A - METHOD FOR PRODUCING Fe-Cr MARTENSITIC STAINLESS STEEL BAR - Google Patents
METHOD FOR PRODUCING Fe-Cr MARTENSITIC STAINLESS STEEL BAR Download PDFInfo
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- 238000004519 manufacturing process Methods 0.000 title claims abstract description 13
- 229910017060 Fe Cr Inorganic materials 0.000 title claims abstract description 11
- 229910002544 Fe-Cr Inorganic materials 0.000 title claims abstract description 11
- UPHIPHFJVNKLMR-UHFFFAOYSA-N chromium iron Chemical compound [Cr].[Fe] UPHIPHFJVNKLMR-UHFFFAOYSA-N 0.000 title claims abstract description 11
- 229910001105 martensitic stainless steel Inorganic materials 0.000 title claims abstract description 9
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 68
- 239000010959 steel Substances 0.000 claims abstract description 68
- 238000005096 rolling process Methods 0.000 claims abstract description 28
- 238000000034 method Methods 0.000 claims description 4
- 238000010438 heat treatment Methods 0.000 abstract description 11
- 239000006227 byproduct Substances 0.000 abstract 1
- 241000270666 Testudines Species 0.000 description 25
- 229910001566 austenite Inorganic materials 0.000 description 10
- 229910000859 α-Fe Inorganic materials 0.000 description 6
- 229910052799 carbon Inorganic materials 0.000 description 3
- 238000007872 degassing Methods 0.000 description 3
- 238000002844 melting Methods 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
- 238000010587 phase diagram Methods 0.000 description 3
- 238000007670 refining Methods 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 2
- 238000005266 casting Methods 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 229910052759 nickel Inorganic materials 0.000 description 2
- 239000002436 steel type Substances 0.000 description 2
- 241000251730 Chondrichthyes Species 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 238000007689 inspection Methods 0.000 description 1
- 239000006249 magnetic particle Substances 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 238000004904 shortening Methods 0.000 description 1
- 229910052710 silicon Inorganic materials 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 230000001629 suppression Effects 0.000 description 1
- 238000011179 visual inspection Methods 0.000 description 1
- 230000037303 wrinkles Effects 0.000 description 1
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Abstract
Description
本発明は、Ｆｅ−Ｃｒ系マルテンサイトステンレス棒鋼の製造方法に関する。 The present invention relates to a method for producing a Fe-Cr martensitic stainless steel bar.
Ｆｅ−Ｃｒ系マルテンサイトステンレス棒鋼として、例えばＳＵＳ４０３圧延棒鋼が挙げられる。ＳＵＳ４０３棒鋼は、Ｃを約０．１％、Ｃｒを約１２％含み、焼入れすると硬くなる鋼種であり、強度が必要とされるシャフト、ボルト等に使用される。この圧延棒鋼の製造方法においては、まず、溶解、精錬、脱ガス等の工程を経て得られた溶鋼が、鋳造により鋼塊（ブルーム）とされる。この鋼塊は、加熱温度１２００〜１３００℃で加熱された後、分塊圧延機へ搬送され、分塊圧延される。分塊圧延では、鋼塊がロールに通されて、断面積が小径化される。分塊圧延された鋼塊は、さらに製品圧延機へ搬送されて圧延され、所定の寸法まで小径化されて、圧延棒鋼が得られる。 Examples of the Fe-Cr martensitic stainless steel bar include SUS403 rolled steel bar. SUS403 steel bar is a steel type that contains about 0.1% C and about 12% Cr and hardens when quenched, and is used for shafts, bolts, and the like that require strength. In this method of manufacturing a rolled steel bar, first, molten steel obtained through processes such as melting, refining, and degassing is made into a steel ingot (bloom) by casting. The steel ingot is heated at a heating temperature of 1200 to 1300 ° C., and then is conveyed to a block rolling mill and subjected to block rolling. In the partial rolling, the steel ingot is passed through a roll, and the cross-sectional area is reduced in diameter. The ingot that has been subjected to the batch rolling is further conveyed to a product rolling mill and rolled, and the diameter is reduced to a predetermined size to obtain a rolled steel bar.
この圧延棒鋼においては、慢性的に、表面に亀甲疵等の表面疵が発生するという問題がある。図４は、亀甲疵を有する圧延棒鋼が示された模式図である。亀甲疵は、図４に示されるように、亀の甲羅の形をした、幅のある密集割れ疵であり、数ｍｍ〜十数ｍｍの深さを有し、長手方向に１〜２列又は全面に発生する。 In this rolled steel bar, there is a problem that surface defects such as turtle shells occur on the surface chronically. FIG. 4 is a schematic view showing a rolled steel bar having a turtle shell. As shown in FIG. 4, the turtle shell is a wide, densely cracked shark shaped like a turtle shell, has a depth of several mm to several tens of mm, and has one or two rows in the longitudinal direction or the entire surface. Occurs.
特開昭５９−１９０３２０号公報には、スラブ段階で１０％以上のデルタフェライト相を有するオーステナイト系ステンレス鋼を熱間圧延して鋼帯とするに際し、１０５０℃〜９００℃の温度域を避けて圧延を行うことで、耳割れを防止するという製造方法の発明について開示されている。この１０５０℃〜９００℃の温度とは、鋼帯における表面温度である。
しかし、上記圧延棒鋼は、スラブ段階で１０％以上のデルタフェライト相を有するオーステナイト系ステンレス鋼ではなく、また、鋼の表面温度が１０５０℃〜９００℃となる温度域を避けて圧延を行った場合でも亀甲疵が発生するという問題がある。 However, the rolled steel bar is not an austenitic stainless steel having a delta ferrite phase of 10% or more in the slab stage, and when rolling is performed while avoiding a temperature range in which the surface temperature of the steel is 1050 ° C. to 900 ° C. But there is a problem that turtle shells occur.
図５は、鋼塊の加熱温度と亀甲疵発生率との関係が示されたグラフである。横軸は、鋼塊の加熱温度、すなわち鋼塊が分塊圧延に供されるときの鋼塊の表面温度であり、縦軸は、亀甲疵発生率である。亀甲疵発生率は、製品圧延、熱処理、矯正後及びピーリング前に磁粉探傷又は目視で外観疵見を行って亀甲疵の有無を観察し、亀甲疵が認められた場合は表面をグラインダーで亀甲疵が無くなる深さまで削って疵深さを確認し、所定のピーリング代では除去出来ない深さを有する亀甲疵をＮＧとしたときのその発生率である。亀甲疵発生率は、圧延された棒鋼の総質量に対する、ＮＧの亀甲疵が発生した棒鋼の質量の百分率である。 FIG. 5 is a graph showing the relationship between the heating temperature of the steel ingot and the incidence of turtle shell. The horizontal axis represents the heating temperature of the steel ingot, that is, the surface temperature of the steel ingot when the steel ingot is subjected to ingot rolling, and the vertical axis represents the turtle shell occurrence rate. The incidence of turtle shell is determined by magnetic particle inspection or visual inspection after product rolling, heat treatment, straightening and peeling, and the presence or absence of turtle shell is observed. This is the occurrence rate when turtle shells having a depth that cannot be removed with a predetermined peeling allowance are determined as NG. The turtle shell occurrence rate is a percentage of the mass of the steel bar in which NG turtle shells are generated with respect to the total mass of the rolled steel bar.
本発明の目的は、表面疵の発生が抑制されて、良好な品質を有するＦｅ−Ｃｒ系マルテンサイトステンレス棒鋼が得られ、歩留も向上する製造方法の提供にある。 An object of the present invention is to provide a production method in which the occurrence of surface flaws is suppressed, a Fe—Cr martensitic stainless steel bar having good quality is obtained, and the yield is improved.
本発明のＦｅ−Ｃｒ系マルテンサイトステンレス棒鋼の製造方法は、
（１）Ｃの含有量が０．０５質量％以上０．１５質量％以下であり、下記数式（１）で表されるＮｉバランスＸが０以上となるように、溶鋼が調製される工程、
（２）調製された溶鋼が鋳造されて、鋼塊が得られる工程、
（３）得られた鋼塊が分塊圧延される工程、
及び
（４）分塊圧延された鋼塊が、さらに圧延される圧延工程
を有する。
The production method of the Fe-Cr martensitic stainless steel bar of the present invention is as follows:
(1) A step in which molten steel is prepared such that the C content is 0.05% by mass or more and 0.15% by mass or less, and the Ni balance X represented by the following formula (1) is 0 or more.
(2) a process in which the prepared molten steel is cast to obtain a steel ingot;
(3) a step in which the obtained steel ingot is rolled into pieces;
And (4) The steel ingot that has been subjected to split rolling has a rolling process in which rolling is further performed.
Ｘ＝Ｎｉ＋２７Ｃ＋２３Ｎ＋０．１Ｍｎ＋０．３Ｃｕ−１．２（Ｃｒ＋Ｍｏ）
−０．５Ｓｉ＋１０ ・・・（１）
但し、数式（１）中の元素記号に、その元素の含有率を代入する。その数値は０以上である。単位は質量％である。この数式（１）において、Ｎｉ、Ｃ、Ｎ、Ｍｎ及びＣｕは、オーステナイト生成元素であり、Ｃｒ、Ｍｏ及びＳｉはフェライト生成元素である。
X = Ni + 27C + 23N + 0.1Mn + 0.3Cu-1.2 (Cr + Mo)
-0.5Si + 10 (1)
However, the content rate of the element is substituted into the element symbol in the formula (1). The numerical value is 0 or more. The unit is mass%. In this numerical formula (1), Ni, C, N, Mn and Cu are austenite generating elements, and Cr, Mo and Si are ferrite generating elements.
本発明に係る製造方法によれば、ＮｉバランスＸが０以上であるので、後述するように鋼塊の組織が圧延加熱時にオーステナイト１相であり、圧延時に安定的に変形し、表面疵が発生するのが抑制される。そして、この場合、鋼塊の温度が１２００℃以上１３００℃以下の状態で分塊圧延に供されても、確実に表面疵が発生するのが抑制される。分塊圧延の後に、さらに製品圧延に供されても、確実に表面疵が発生するのが抑制される。従って、本発明によれば、良好な品質を有するＦｅ−Ｃｒ系マルテンサイトステンレス棒鋼が得られ、歩留も向上する。 According to the production method of the present invention, since Ni balance X is 0 or more, as will be described later, the structure of the steel ingot is austenite 1 phase during rolling and heating, and is stably deformed during rolling and surface flaws are generated. To be suppressed. In this case, even when the steel ingot is subjected to ingot rolling in a state where the temperature of the steel ingot is 1200 ° C. or higher and 1300 ° C. or lower, the occurrence of surface defects is reliably suppressed. Even if it is subjected to product rolling after the block rolling, the generation of surface flaws is reliably suppressed. Therefore, according to this invention, the Fe-Cr type | system | group martensitic stainless steel bar which has favorable quality is obtained, and a yield improves.
以下、適宜図面が参照されつつ、好ましい実施形態に基づいて本発明が詳細に説明される。 Hereinafter, the present invention will be described in detail based on preferred embodiments with appropriate reference to the drawings.
図１は、Ｆｅ−Ｃｒ系マルテンサイトステンレス棒鋼としてのＳＵＳ４０３圧延棒鋼の製造方法が示されたフローチャートである。この製造方法においては、まず、溶解、精錬及び脱ガス処理を経て、Ｃの含有量が０．０５質量％以上０．１５質量％以下であり、上記数式（１）で表されるＮｉバランスＸが０以上となるように、溶鋼が調製される製鋼工程が実施される（ＳＴＥＰ１）。このＮｉバランスＸは、好ましくは、０．１以上となるようにする。調製された溶鋼は、鋳造機へ搬送され、鋳造されて、鋼塊が得られる（ＳＴＥＰ２）。 FIG. 1 is a flowchart showing a method for producing a SUS403 rolled steel bar as an Fe—Cr martensitic stainless steel bar. In this production method, first, through melting, refining and degassing treatment, the C content is 0.05 mass% or more and 0.15 mass% or less, and the Ni balance X represented by the above formula (1) The steelmaking process in which the molten steel is prepared is performed so that the value becomes 0 or more (STEP 1). The Ni balance X is preferably set to 0.1 or more. The prepared molten steel is conveyed to a casting machine and cast to obtain a steel ingot (STEP 2).
次に、この鋼塊が加熱炉へ搬送され、加熱温度１２００℃以上１３００℃以下で加熱される（ＳＴＥＰ３）。加熱された鋼塊は、表面温度１２００℃以上１３００℃以下を有した状態で、分塊圧延機へ搬送され、所定の上り角に分塊圧延される（ＳＴＥＰ４）。引き続き、製品圧延され、所定の寸法まで小径化されて、圧延棒鋼が得られる（ＳＴＥＰ５）。そして、圧延棒鋼は冷却される（ＳＴＥＰ６）。 Next, this steel ingot is conveyed to a heating furnace and heated at a heating temperature of 1200 ° C. or higher and 1300 ° C. or lower (STEP 3). The heated steel ingot is conveyed to a block mill with a surface temperature of 1200 ° C. or more and 1300 ° C. or less, and is batch-rolled to a predetermined upward angle (STEP 4). Subsequently, the product is rolled, and the diameter is reduced to a predetermined size to obtain a rolled steel bar (STEP 5). Then, the rolled steel bar is cooled (STEP 6).
図２は、Ｃの含有量が０．１質量％であるときのＦｅ−Ｃｒ合金の状態図である。図２中、γはオーステナイト相、γ＋αは、オーステナイト相とフェライト相との２相域である。 FIG. 2 is a phase diagram of the Fe—Cr alloy when the C content is 0.1 mass%. In FIG. 2, γ is an austenite phase, and γ + α is a two-phase region of an austenite phase and a ferrite phase.
圧延時、鋼塊の組織が上記２相である場合、亀甲疵は、鋼塊表面部においてフェライト相に沿って生じることが確認されている。フェライト相は高温で柔らかく伸び、オーステナイト相は伸びにくいので、圧延時に亀裂が生じると考えられる。鋼塊の組織がオーステナイト１相である場合は、圧延時に鋼塊は安定的に変形し、亀裂が生じず、亀甲疵が発生するのが抑制される。 At the time of rolling, when the structure of the steel ingot is the above-mentioned two phases, it has been confirmed that the turtle shell is formed along the ferrite phase at the surface of the steel ingot. The ferrite phase is softly stretched at high temperatures and the austenite phase is difficult to stretch, so it is considered that cracking occurs during rolling. When the structure of the steel ingot is an austenite single phase, the steel ingot is stably deformed during rolling, cracks are not generated, and generation of turtle shells is suppressed.
鋼塊の加熱温度は、圧延時間短縮及び圧延機モーター負荷の観点から、１２００℃以上１３００℃以下とされるのが好ましく、この温度範囲においても、鋼塊の組織が安定的にオーステナイト１相となるようにする必要がある。図２の状態図を例にとると、鋼塊の成分のうちＣｒの含有量を少なくして、鋼塊の状態が、境界線より下側に位置するように、すなわち、ＮｉバランスＸが０以上になるように調製する。ＮｉバランスＸが０以上である場合、表面温度が１２００℃以上１３００℃以下であっても、鋼塊の組織はオーステナイト１相であるので、亀甲疵の発生が抑制される。ＮｉバランスＸの調製は、Ｃｒ以外の上記数式（１）の元素を用いてもなされ得る。ＮｉバランスＸが０以上になるように、Ｃの含有量を多くした場合、状態図において境界線が右側にシフトしてオーステナイト１相の領域が拡がり、鋼塊の組織が確実にオーステナイト１相となる。 The heating temperature of the steel ingot is preferably 1200 ° C. or higher and 1300 ° C. or lower from the viewpoint of shortening the rolling time and the rolling mill motor load, and even in this temperature range, the steel ingot structure is stable with the austenite 1 phase. It is necessary to be. Taking the state diagram of FIG. 2 as an example, the Cr content of the steel ingot components is reduced so that the state of the steel ingot is located below the boundary line, that is, the Ni balance X is 0. Prepare as above. When the Ni balance X is 0 or more, even if the surface temperature is 1200 ° C. or more and 1300 ° C. or less, the structure of the steel ingot is an austenite single phase, so that the formation of turtle shell is suppressed. The Ni balance X can also be prepared using an element of the above formula (1) other than Cr. When the content of C is increased so that the Ni balance X becomes 0 or more, the boundary line shifts to the right side in the phase diagram and the region of the austenite 1 phase expands, and the structure of the steel ingot is surely changed to the austenite 1 phase. Become.
図３は、ＮｉバランスＸと亀甲疵発生率との関係が示されたグラフである。横軸は、ＮｉバランスＸであり、縦軸は亀甲疵発生率である。図３より、ＮｉバランスＸがプラスである場合、亀甲疵が発生しないことが確認された。その結果、品質が向上するとともに、歩留も向上したことが確認されている。 FIG. 3 is a graph showing the relationship between the Ni balance X and the turtle shell incidence. The horizontal axis is the Ni balance X, and the vertical axis is the turtle shell incidence. From FIG. 3, it was confirmed that when the Ni balance X is positive, no turtle shell is generated. As a result, it was confirmed that the quality was improved and the yield was also improved.
以下、実施例によって本発明の効果が明らかにされるが、この実施例の記載に基づいて本発明が限定的に解釈されるべきではない。 Hereinafter, the effects of the present invention will be clarified by examples. However, the present invention should not be construed in a limited manner based on the description of the examples.
［実施例１］
溶解工程、精錬工程及び脱ガス工程を経て、表１に示されるように、化学成分としてＮｉを０．２５質量％、Ｃを０．１２６質量％、Ｎを４９９質量ｐｐｍ、Ｍｎを０．５０質量％、Ｃｕを０．０７質量％、Ｃｒを１１．５７質量％、Ｍｏを０．１７質量％及びＳｉを０．３３質量％含み、残部としてＦｅ及び不可避不純物を含むＳＵＳ４０３溶鋼を調製した。この溶鋼のＮｉバランスＸは、０．５６８である。次に、調製した溶鋼を鋳造し、鋼塊を得た。この鋼塊を加熱炉で１２７５℃に加熱した後、分塊圧延機へ搬送し、分塊圧延した。分塊圧延した鋼塊は製品圧延し、直径１０３ｍｍの圧延棒鋼を得た。そして、圧延棒鋼を冷却した。
[Example 1]
After melting, refining and degassing steps, as shown in Table 1, 0.25 mass% Ni, 0.126 mass% C, 499 mass ppm N, and 0.50 Mn as chemical components A SUS403 molten steel containing 10% by mass, 0.07% by mass of Cu, 11.57% by mass of Cr, 0.17% by mass of Mo and 0.33% by mass of Si, and the balance containing Fe and inevitable impurities was prepared. The Ni balance X of this molten steel is 0.568. Next, the prepared molten steel was cast to obtain a steel ingot. The steel ingot was heated to 1275 ° C. in a heating furnace, and then conveyed to a block mill and subjected to block rolling. The ingot that has been subjected to split rolling was rolled to obtain a rolled steel bar having a diameter of 103 mm. And the rolled steel bar was cooled.
［実施例２から３及び比較例１から３］
組成を上記表１に示される通りとした他は実施例１と同様にして、圧延棒鋼を得た。
[Examples 2 to 3 and Comparative Examples 1 to 3]
A rolled steel bar was obtained in the same manner as in Example 1 except that the composition was as shown in Table 1 above.
［亀甲疵の評価］
上記実施例及び比較例につき、亀甲疵発生率を求めた。その結果が上記表１に示される。
[Evaluation of turtle shell]
About the said Example and comparative example, the turtle shell incidence rate was calculated | required. The results are shown in Table 1 above.
表１に示されるように、ＮｉバランスＸが０以上である各実施例の亀甲疵発生率は０％であり、本発明の優位性は明らかである。 As shown in Table 1, the turtle shell occurrence rate of each example in which the Ni balance X is 0 or more is 0%, and the superiority of the present invention is clear.
本発明に係る製造方法は、ＳＵＳ４０３鋼に限定されず、ＳＵＳ４１０等の他の鋼種にも適用され得る。また、丸棒鋼にも限定されず、角棒等の他の棒鋼にも適用され得る。そして、亀甲疵以外の表面疵の抑制にも適用され得る。 The production method according to the present invention is not limited to SUS403 steel, but can be applied to other steel types such as SUS410. Moreover, it is not limited to round bar steel, It can apply also to other steel bars, such as a square bar. And it can apply also to suppression of surface wrinkles other than a turtle shell.
Claims (1)
調製された溶鋼が鋳造されて、鋼塊が得られる工程と、
得られた鋼塊が分塊圧延される工程と、
分塊圧延された鋼塊が、さらに圧延される圧延工程と
を有する、Ｆｅ−Ｃｒ系マルテンサイトステンレス棒鋼の製造方法。
Ｘ＝Ｎｉ＋２７Ｃ＋２３Ｎ＋０．１Ｍｎ＋０．３Ｃｕ−１．２（Ｃｒ＋Ｍｏ）
−０．５Ｓｉ＋１０ ・・・（１）
但し、数式（１）中の元素記号に、その元素の含有率を代入する。単位は、質量％である。
A step in which the molten steel is prepared such that the content of C is 0.05% by mass or more and 0.15% by mass or less, and the Ni balance X represented by the following mathematical formula (1) is 0 or more;
A process in which the prepared molten steel is cast to obtain a steel ingot;
A step in which the obtained steel ingot is subjected to partial rolling;
The manufacturing method of the Fe-Cr type | system | group martensitic stainless steel bar which has the rolling process in which the steel ingot by which the piece rolling was carried out is further rolled.
X = Ni + 27C + 23N + 0.1Mn + 0.3Cu-1.2 (Cr + Mo)
-0.5Si + 10 (1)
However, the content rate of the element is substituted into the element symbol in the formula (1). The unit is mass%.
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102876854A (en) * | 2012-10-12 | 2013-01-16 | 上海电机学院 | Tempering treatment technical method for 1Cr12 martensite stainless steel pressure spring forge piece |
| WO2020196595A1 (en) * | 2019-03-27 | 2020-10-01 | 日鉄ステンレス株式会社 | Steel rod |
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| JPH06100930A (en) * | 1992-09-17 | 1994-04-12 | Kawasaki Steel Corp | Production of round billet for producing martensitic stainless seamless pipe |
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| JP2003231951A (en) * | 2002-02-07 | 2003-08-19 | Sanyo Special Steel Co Ltd | High-strength precipitation-hardening stainless steel, stainless steel wire and high-strength fastening member using this steel wire |
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102876854A (en) * | 2012-10-12 | 2013-01-16 | 上海电机学院 | Tempering treatment technical method for 1Cr12 martensite stainless steel pressure spring forge piece |
| WO2020196595A1 (en) * | 2019-03-27 | 2020-10-01 | 日鉄ステンレス株式会社 | Steel rod |
| JPWO2020196595A1 (en) * | 2019-03-27 | 2020-10-01 | ||
| JP7077477B2 (en) | 2019-03-27 | 2022-05-30 | 日鉄ステンレス株式会社 | Ferritic stainless steel rod-shaped steel |
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| JP5009520B2 (en) | 2012-08-22 |
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