JP5674313B2 - Composite structure steel and heat treatment method for providing the same - Google Patents
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- 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
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- 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- 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
- C21D2211/001—Austenite
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- 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
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Description
本発明は、複合組織鋼及びそれを提供するための熱処理方法に関する。より詳細には、常温でオーステナイトが残留し、マルテンサイトプレートの大きさが微細で、靭性及び強度が向上した残留オーステナイト及びＨＣＰマルテンサイト組織が混合された複合組織鋼及びそれを提供するための熱処理方法に関する。 The present invention relates to a composite structure steel and a heat treatment method for providing the same . More specifically, austenite remains at room temperature, the martensite plate has a fine size, and the composite austenite and HCP martensite structure mixed with improved toughness and strength, and heat treatment for providing the same Regarding the method.
常温残留オーステナイトを利用する代表的な鋼としては、ＴＲＩＰ鋼（ＴＲａｎｓｆｏｒｍａｔｉｏｎ Ｉｎｄｕｃｅｄ Ｐｌａｓｔｉｃｉｔｙ）が知られている。 TRIP steel (Transformation Induced Plasticity) is known as a typical steel that uses room temperature retained austenite.
ＴＲＩＰ鋼は、主に低炭素鋼領域でフェライト（Ｆｅｒｒｉｔｅ）及びベイナイト（Ｂａｉｎｉｔｅ）の相変態によって基地に固溶された炭素を残留オーステナイトに濃縮させることによって常温で安定した残留オーステナイトを製造する方法によって得られる。 TRIP steel is mainly produced in the low carbon steel region by the method of producing stable austenite at room temperature by concentrating carbon dissolved in the matrix into residual austenite by the phase transformation of ferrite and bainite. can get.
また、最近注目されているＱｕｅｎｃｈｉｎｇ＆Ｐａｒｔｉｔｉｏｎｉｎｇ法によれば、マルテンサイト変態開始温度（Ｍｓ）及び変態終了温度（Ｍｆ）の間で急冷後に１段または２段に等温維持して生成されたマルテンサイト相の内部に存在する炭素を残留オーステナイトに移動させて、常温で安定した状態で炭素を濃縮させることによって、常温で強度及び靭性が優れている鋼を製造することができる。 In addition, according to the Quenching & Partitioning method which has recently attracted attention, martensite produced by maintaining isothermally in one or two stages after rapid cooling between the martensite transformation start temperature (M s ) and the transformation end temperature (M f ). By transferring the carbon present in the phase to residual austenite and concentrating the carbon in a stable state at room temperature, a steel having excellent strength and toughness at room temperature can be produced.
しかし、この場合、常温以上のできるだけ高い温度でパティショニングを行うことによってのみ炭素の移動が促進されるので、鋼の製造過程中に鋼を加熱維持する設備が必要であり、加熱維持に所定の時間がかかるので、生産性の増加に制約があり、製造費用が増加する問題がある。 However, in this case, since the movement of carbon is promoted only by partitioning at a temperature as high as possible above room temperature, an equipment for heating and maintaining the steel during the steel manufacturing process is required. Since time is required, there is a problem that the increase in productivity is limited and the manufacturing cost increases.
他方で、ニッケル（Ｎｉ）やクロム（Ｃｒ）などが多量に添加された高合金鋼を利用して常温で残留オーステナイトを含む鋼を製造した研究事例が多数あり、また合金鋼における種々の成分のマルテンサイト変態開始温度（Ｍ ｓ ）への影響についても研究されている（非特許文献１）が、実際には、常温で残留オーステナイトを残留させるために高価な合金元素を多量に添加しなければならないので、製造費用が増加して、経済性が低下する問題がある。 Various components in the other hand, nickel (Ni) or chromium (Cr), etc. is Ri Ah example study produced a steel containing retained austenite many at room temperature using high alloy steels which are added in large amounts, also alloy steel The effect on the martensitic transformation start temperature (M s ) has been studied (Non-Patent Document 1) . In practice, however, a large amount of expensive alloy elements must be added to leave residual austenite at room temperature. Therefore, there is a problem that the manufacturing cost increases and the economic efficiency decreases.
本発明は、このような問題を解決するために発明されたものであって、マンガン（Ｍｎ）を除く他の合金成分の含有量を制限する代わりに、マルテンサイト逆変態を利用して、マルテンサイト変態開始温度を低くして、常温でオーステナイトが残留し、マルテンサイトプレートの大きさが微細で、靭性及び強度が向上した複合組織鋼を提供することを目的とする。 The present invention has been invented to solve such problems, and uses martensite reverse transformation instead of limiting the content of other alloy components except manganese (Mn) to by lowering the site transformation start temperature, the austenite may remain at ambient temperature, the size of the martensite plates fine, and purpose thereof is to provide a composite structure steel toughness and strength is improved.
前記目的を達成するための本発明の一実施例によれば、複合組織鋼は、質量％基準で、Ｃ：０．５以下、Ｍｎ：１５超過３５以下、Ｃｏ、Ｔｉ、及びＡｌのうちのいずれか１つ以上の合計：３以下、Ｃｒ、Ｃｕ、Ｍｏ、Ｎｉ、Ｎｂ、Ｓｉ、及びＶのうちのいずれか１つ以上の合計：１０以下、残りはＦｅ、及びその他のやむをえずに添加される不純物からなる。 According to one embodiment of the present invention to achieve the pre-Symbol purpose, composite structure steel, in mass% basis, C: 0.5 or less, Mn: 15 exceeded 35 below, Co, Ti, and A l any one or more of the total of: 3 or less, Cr, Cu, Mo, Ni , Nb, Si, and any one or more of the total of the V: 10 or less, and the remainder Fe, and unavoidable other It consists of impurities added without.
前記複合組織鋼は、残留オーステナイト及びＨＣＰマルテンサイト組織が混合されたものである。前記複合組織鋼は、前記合金成分の含有量が「ＭＳ＝２６０−３３０Ｃ＋２Ａｌ＋７Ｃｏ−１４Ｃｒ−１３Ｃｕ−１９（Ｍｎ−１５）−５Ｍｏ−４Ｎｂ−１３Ｎｉ−７Ｓｉ＋３Ｔｉ−４Ｖ」であるＭＳ式の値は５０乃至１２０である。Ｃ、Ｍｎ、Ｓｉ、Ｎｉ、Ｐ、及びＳの含有量は質量％で各々約０．３０、約２０．５０、約０．１８、約０．０２、約０．００３、及び約０．００１７であり、ＭＳ値は約５３．４４である。 The composite structure steel is a mixture of retained austenite and HCP martensite structure. The composite structure steel, the value of MS-type content is "MS = 260-330C + 2Al + 7Co- 14Cr-13Cu-19 (Mn-15) -5Mo-4Nb-13Ni-7Si + 3Ti-4V " in the alloy component 50 to 120. C, Mn, Si, Ni, each about 0.30 at a content mass% of P, and S, about 20.50, about 0.18, about 0.02, about 0.003, and about 0.0017 And the MS value is about 53.44.
前記目的を達成するための本発明の一実施例によれば、質量％基準で、Ｃ：０．５以下、Ｍｎ：１５超過３５以下、Ｃｏ、Ｔｉ及びＡｌのうちのいずれか１つ以上の合計：３以下、Ｃｒ、Ｃｕ、Ｍｏ、Ｎｉ、Ｎｂ、Ｓｉ、及びＶのうちのいずれか１つ以上の合計：１０以下、残りはＦｅ、及びその他のやむをえずに添加される不純物からなり、前記合金成分の含有量が下記のＭＳ式、
ＭＳ＝２６０−３３０Ｃ＋２Ａｌ＋７Ｃｏ−１４Ｃｒ−１３Ｃｕ−１９（Ｍｎ−１５）−５Ｍｏ−４Ｎｂ−１３Ｎｉ−７Ｓｉ＋３Ｔｉ−４Ｖ
において５０乃至１２０の値を満たす鋼を熱間圧延して、鋼材を製造する段階、そして前記鋼材を加熱して焼入れして、マルテンサイト組織を含むように急冷する１次焼入段階を行う。その後、前記焼入れした鋼材を加熱した後で焼入れして、逆変態されたオーステナイト結晶粒の大きさを微細化する２次焼入段階を行う。次に、前記２次焼入段階後に前記鋼材を急冷して、ＨＣＰマルテンサイトを生成する急冷段階を行う。
According to one embodiment of the present invention to achieve the pre-Symbol purposes, in mass% basis, C: 0.5 or less, Mn: 15 exceeded 35 below, Co, one of Ti and A l 1 Sum of one or more: 3 or less, sum of any one or more of Cr, Cu, Mo, Ni, Nb, Si, and V: 10 or less, the rest is Fe, and other impurities that are unavoidably added The content of the alloy component is the following MS formula,
MS = 260-330C + 2Al + 7Co-14Cr-13Cu-19 (Mn-15) -5Mo-4Nb-13Ni-7Si + 3Ti-4V
The steel satisfying the value of 50 to 120 is hot-rolled to produce a steel material, and the steel material is heated and quenched, followed by a primary quenching step of quenching to include a martensite structure. Thereafter, a second quenching step is performed in which the quenched steel material is heated and then quenched to refine the size of the reverse transformed austenite crystal grains. Then quenched the steel after the second quenching step, intends row quenched generating a HCP martensite.
前記複合組織鋼を提供するための熱処理をするために、急冷段階後に前記鋼材を常温に維持する段階をさらに含む。前記複合組織鋼は、残留オーステナイト及びＨＣＰマルテンサイト組織が混合されたものである。 To the heat treatment to provide the composite structure steel, further comprising the step of maintaining the steel at room temperature after quenching step. Before SL composite structure steel are those retained austenite and HCP martensite is mixed.
前記複合組織鋼は、前記合金成分の含有量が「ＭＳ＝２６０−３３０Ｃ＋２Ａｌ＋７Ｃｏ−１４Ｃｒ−１３Ｃｕ−１９（Ｍｎ−１５）−５Ｍｏ−４Ｎｂ−１３Ｎｉ−７Ｓｉ＋３Ｔｉ−４Ｖ」であるＭＳ式の値は約５０乃至約１２０である。Ｃ、Ｍｎ、Ｓｉ、Ｎｉ、Ｐ、及びＳの含有量は質量％で各々約０．３０、約２０．５０、約０．１８、約０．０２、約０．００３、及び約０．００１７であり、ＭＳ値は約５３．４４である。 The composite structure steel, the value of the content is "MS = 260-330C + 2Al + 7Co- 14Cr-13Cu-19 (Mn-15) -5Mo-4Nb-13Ni-7Si + 3Ti-4V " Der Ru M S type of the alloy components About 50 to about 120. C, Mn, Si, Ni, each about 0.30 at a content mass% of P, and S, about 20.50, about 0.18, about 0.02, about 0.003, and about 0.0017 And the MS value is about 53.44.
前記２次焼入段階で、前記１次焼入段階で焼入れされた鋼材は、オーステナイト逆変態開始温度（Ａｓ）以上約８００℃以下の範囲で加熱される。 In the secondary quenching stage, the steel material quenched in the primary quenching stage is heated in the range of the austenite reverse transformation start temperature (A s ) or more and about 800 ° C. or less.
前記２次焼入段階後に前記鋼材を急冷する段階は、常温（２５℃）以下の冷媒を使用する。 The step of rapidly cooling the steel material after the secondary quenching step uses a refrigerant having a normal temperature (25 ° C.) or less.
本発明によれば、常温でオーステナイトが残留し、マルテンサイトプレートの大きさが微細で、複合組織鋼の靭性及び強度が向上する効果がある。 According to the present invention, austenite remains at room temperature, the size of the martensite plate is fine, and the toughness and strength of the composite structure steel are improved.
以下、本発明の実施例を添付した図面を参照して詳細に説明する。まず、各図面の構成要素に参照符号を付ける際には、同一な構成要素に対してはたとえ異なる図面上に表示されていてもできるだけ同一な符号を付けるようにした。また、本発明を説明する際には、関連する公知の構成または機能に対する具体的な説明が本発明の要旨をあいまいにすると判断される場合には、その詳細な説明は省略した。 Hereinafter, embodiments of the present invention will be described in detail with reference to the accompanying drawings. First, when the reference numerals are given to the constituent elements of each drawing, the same constituent elements are given the same reference numerals as much as possible even if they are displayed on different drawings. In the description of the present invention, when it is determined that a specific description of a related known configuration or function may obscure the gist of the present invention, the detailed description thereof is omitted.
本発明の実施例による複合組織鋼は、Ｃ、Ｍｎ、Ｃｏ、Ｔｉ、Ａｌ、Ｍｏ、Ｎｉ、Ｎｂ、Ｓｉ、Ｖ、残りはＦｅ、及びやむをえずに添加される不純物からなる合金成分を含む。 A composite structure steel according to an embodiment of the present invention includes an alloy component composed of C, Mn, Co, Ti, Al , Mo, Ni, Nb, Si, V, the rest Fe, and impurities that are unavoidably added. .
より具体的に、本発明の実施例による複合組織鋼は、質量％基準で、Ｃ：０．５以下、Ｍｎ：１５超過３５以下、Ｃｏ、Ｔｉ、及びＡｌのうちのいずれか１つ以上の合計：３以下、Ｃｒ、Ｃｕ、Ｍｏ、Ｎｉ、Ｎｂ、Ｓｉ、及びＶのうちのいずれか１つ以上の合計：１０以下、残りはＦｅ、及びその他のやむをえずに添加される不純物からなる。 More specifically, the composite structure steel according to an embodiment of the present invention, in mass% basis, C: 0.5 or less, Mn: 15 exceeded 35 below, Co, Ti, and any one or more of A l Total: 3 or less, total of any one or more of Cr, Cu, Mo, Ni, Nb, Si, and V: 10 or less, the remainder consists of Fe and other impurities that are unavoidably added .
特に、本発明の実施例による複合組織鋼において、合金成分の質量％での含有量を変数にして計算されるＭＳ値は、下記の式１で示される。
ＭＳ＝２６０−３３０Ｃ＋２Ａｌ＋７Ｃｏ−１４Ｃｒ−１３Ｃｕ−１９（Ｍｎ−１５）−５Ｍｏ−４Ｎｂ−１３Ｎｉ−７Ｓｉ＋３Ｔｉ−４Ｖ−−−−−（式１）
In particular, in the composite structure steel according to the example of the present invention, the MS value calculated by using the content in mass % of the alloy component as a variable is represented by the following formula 1.
MS = 260-330C + 2Al + 7Co-14Cr-13Cu-19 (Mn-15) -5Mo-4Nb-13Ni-7Si + 3Ti-4V ----- (Formula 1)
ここで、式１はイシダが非特許文献１において提案したマルテンサイト生成温度式に基づいてマンガン（Ｍｎ）の影響を調査し、これを補正して導き出された式である。 Here, Equation 1 will investigate the effect of manganese (Mn) based on the martensite formation temperature equation Issy Da proposed in Non-Patent Document 1, an equation derived by correcting this.
一方、マルテンサイト変態開始温度（Ｍｓ）は、組成の影響だけでなく、オーステナイト結晶粒の大きさの影響も受ける。 On the other hand, the martensitic transformation start temperature (M s ) is influenced not only by the composition but also by the size of the austenite crystal grains.
つまり、オーステナイト結晶粒の大きさが微細になれば、マルテンサイト変態開始温度が低くなるが、これは、オーステナイト結晶粒の微細化による母相強化効果によって、鋼がマルテンサイト変態する時に必須の剪断変形に必要なエネルギーが増加するので、これを補充するために変態に必要な駆動力が追加的に要求されるためである。 In other words, if the austenite grain size becomes finer, the martensite transformation start temperature becomes lower. This is due to the effect of strengthening the parent phase due to the refinement of the austenite grain, which is essential when the steel undergoes martensite transformation. This is because the energy required for the deformation increases, so that a driving force necessary for the transformation is additionally required to supplement the energy.
一方、本発明の実施例においては、組成を制限するためのパラメータとしてだけ式１を使用した。 On the other hand, in the examples of the present invention, Equation 1 was used only as a parameter for limiting the composition.
本発明の実施例において、ＭＳ値が５０〜１２０の範囲に該当するように組成を制限したのは、マルテンサイト逆変態によるオーステナイト結晶粒の微細化によって、実際のマルテンサイト変態開始温度を式１より約１０〜４０℃程度低くした状況で、適当な分率のＨＣＰマルテンサイトを製造するためである。 In the examples of the present invention, the composition was limited so that the MS value was in the range of 50 to 120. The actual martensite transformation start temperature was expressed by the formula 1 by refining austenite crystal grains by martensite reverse transformation. This is because an HCP martensite having an appropriate fraction is produced in a state where the temperature is lowered by about 10 to 40 ° C.
ＭＳ値が５０以下である場合には、十分な量のマルテンサイトを生成することができないので、鋼の強度が低くなる。 When the MS value is 50 or less, since a sufficient amount of martensite cannot be generated, the strength of the steel is lowered.
反面、ＭＳ値が１２０を超える場合には、オーステナイト結晶粒の微細化によって、実際のマルテンサイト変態開始温度（Ｍｓ）を低くしても、常温で残留する残留オーステナイトの量が非常に少なくなるので、十分な靭性増加効果を得ることができない。 On the other hand, when the MS value exceeds 120, the amount of residual austenite remaining at room temperature becomes very small even if the actual martensite transformation start temperature (M s ) is lowered due to the refinement of austenite crystal grains. Therefore, a sufficient toughness increasing effect cannot be obtained.
炭素（Ｃ）の含有量は０．５質量％以下程度に制限すればよく、それより多く含まれる場合には、他の合金元素の含有量を調節しても、本発明の目的である複合組織鋼を製造するのが難しい。 The content of carbon (C) may be limited to about 0.5% by mass or less, and when it is contained more than that, even if the content of other alloy elements is adjusted, the composite which is the object of the present invention Difficult to produce textured steel.
また、炭素が多く含まれる場合には、積層欠陥エネルギー（Ｓｔａｃｋｉｎｇ Ｆａｕｌｔ Ｅｎｅｒｇｙ）が増加するので、熱処理後にＨＣＰマルテンサイトでなくＢＣＴマルテンサイトが生成されるおそれがある。 In addition, when a large amount of carbon is contained, stacking fault energy increases, so that there is a possibility that BCT martensite is generated instead of HCP martensite after heat treatment.
一方、マンガン（Ｍｎ）の含有量が１５質量％を超えるように制限した理由は、常温でＨＣＰ構造のマルテンサイトを生成するためである。 On the other hand, the reason for restricting the manganese (Mn) content to exceed 15% by mass is to generate HCP-structured martensite at room temperature.
一方、マンガンの含有量は３５質量％以下であるのが好ましい。 On the other hand, the manganese content is preferably 35% by mass or less.
つまり、ＨＣＰマルテンサイトは、一種の準安定相（Ｍｅｔａｓｔａｂｌｅ Ｐｈａｓｅ）であって、応力によってＢＣＣまたはＢＣＴ構造に変態するので、靭性の向上に大きく寄与するが、結晶粒の微細化を考慮すれば、マンガン（Ｍｎ）の含有量が１５質量％以下である場合には、ＨＣＰ構造のマルテンサイトが十分な量に生成されずに、靭性増加効果が微小である。 That is, HCP martensite is a kind of metastable phase and transforms into a BCC or BCT structure by stress, so it greatly contributes to the improvement of toughness. When the content of manganese (Mn) is 15% by mass or less, martensite having an HCP structure is not generated in a sufficient amount, and the effect of increasing toughness is minute.
一方、前記数値は、Ｆｅ−Ｍｎ−Ｃ系合金及びＦｅ−Ｍｎ−Ｃ−（少量のＮｉ、Ｃｒ）系合金に対する実験結果から推定された値である。 On the other hand, the said numerical value is the value estimated from the experimental result with respect to a Fe-Mn-C type | system | group alloy and a Fe-Mn-C- (a small amount of Ni, Cr) type | system | group alloy.
合金成分であるＣｒ、Ｃｕ、Ｍｏ、Ｎｉ、Ｎｂ、Ｓｉ、及びＶの各含有量を合計した総含有量を１０質量％以下に制限した理由は、下記の通りである。 The reason for limiting the total content of the alloy components Cr, Cu, Mo, Ni, Nb, Si, and V to 10% by mass or less is as follows.
ニッケル（Ｎｉ）やクロム（Ｃｒ）などの合金成分を多く含む高合金鋼でない一般鋼において、マルテンサイト変態開始温度（Ｍｓ）は常温から非常に上側に上がっている。したがって、常温でオーステナイト及びマルテンサイト組織が混合された複合組織鋼を製造するためには、合金元素を添加して、マルテンサイト変態開始温度（Ｍｓ）を低くしなければならない。つまり、前記合金元素を多量に含めば、本発明で提案したＭＳ値の範囲に合わせることができ、常温で残留オーステナイトを製造することはできるが、本発明が目的とする組織である残留オーステナイト及びＨＣＰマルテンサイトの複合組織鋼を製造することはできない。 In a general steel that is not a high alloy steel containing a large amount of alloy components such as nickel (Ni) and chromium (Cr), the martensitic transformation start temperature (M s ) is very high from normal temperature. Therefore, in order to manufacture a composite structure steel in which austenite and martensite structure are mixed at room temperature, an alloy element must be added to lower the martensite transformation start temperature (M s ). That is, if a large amount of the alloy element is included, the MS value range proposed in the present invention can be adjusted, and residual austenite can be produced at room temperature. HCP martensite composite steel cannot be produced.
また、前記合金元素は大部分が高価であるので、これらを多量に含む場合には、経済性が低下する問題が付加的に発生する。 In addition, since most of the alloy elements are expensive, when they are contained in large quantities, there is an additional problem that the economy is reduced.
次に、本発明の実施例による複合組織鋼を提供するための熱処理方法について説明する。 Next, a heat treatment method for providing a composite steel according to an embodiment of the present invention will be described.
本発明の実施例による常温残留オーステナイト及びＨＣＰマルテンサイトの複合組織鋼は、上記組成を満たす鋼が溶融されて溶鋼に製造され、連続鋳造されてスラブ（ｓｌａｂ）に鋳造された後、加熱炉で再加熱されて熱間圧延によって板材に製造される。 The normal-temperature retained austenite and HCP martensite composite steel according to an embodiment of the present invention is manufactured by melting a steel satisfying the above composition into a molten steel, continuously casting it into a slab, and then heating it in a heating furnace. It is reheated and manufactured into a plate material by hot rolling.
また、その後、必要に応じて冷間圧延及び焼鈍熱処理、板金工程を経て製品の形状に製造される。 Moreover, after that, it is manufactured into the shape of the product through cold rolling, annealing heat treatment, and sheet metal process as necessary.
まず、前記鋼を焼入熱処理炉に維持した後、冷却媒（冷却水、冷却油など）を利用して急冷して、焼入れ熱処理する。この過程でマルテンサイト組織が生成され、このように処理された鋼材を再びオーステナイト逆変態開始温度（Ａｓ）以上８００℃以下で焼入れする。このように焼入及び急冷後に逆変態させるのは、マルテンサイト状態での逆変態によって、逆変態されたオーステナイトの結晶粒の大きさを微細化させるためである。 First, after maintaining the steel in a quenching heat treatment furnace, the steel is quenched using a cooling medium (cooling water, cooling oil, etc.) and subjected to a quenching heat treatment. In this process, a martensite structure is generated, and the steel material thus treated is again quenched at an austenite reverse transformation start temperature (A s ) or higher and 800 ° C. or lower. The reason why reverse transformation is performed after quenching and quenching is to reduce the size of the reverse transformed austenite crystal grains by the reverse transformation in the martensite state.
マルテンサイト組織は、内部に多数のプレート（ｐｌａｔｅ）境界及び電位を含む組織であって、サブグレインバウンダリー（Ｓｕｂ−ｇｒａｉｎ ｂｏｕｎｄａｒｙ）に相当する核生成部が多量に存在するので、逆変態時に結晶粒の大きさが微細になる。 The martensite structure includes a large number of plate boundaries and potentials inside, and a large amount of nucleation parts corresponding to a sub-grain boundary (sub-boundary) exist, so that a crystal is formed during reverse transformation. The grain size becomes fine.
また、逆変態時に再焼入温度を逆変態開始温度（Ａｓ）以上８００℃以下に維持する理由は、逆変態されたオーステナイト組織を製造しても、微細な結晶粒が焼入れ途中に成長するのをできるだけ防止して、微細な結晶粒を維持するためである。 The reason for maintaining the re-quenching temperature at the reverse transformation start temperature (A s ) or higher and 800 ° C. or lower at the time of reverse transformation is that fine crystal grains grow during quenching even if a reverse transformed austenite structure is produced. This is to prevent fine particles as much as possible and maintain fine crystal grains.
一方、逆変態された鋼を常温（２５℃）以下の氷水などの冷媒を使用して急冷させた後で常温に維持するのは、適当量のＨＣＰマルテンサイトを生成して、常温で残留オーステナイトを保存するためである。一方、急冷時の冷媒の温度は、所望の強度水準によって調節することができる。もちろん、この時の延伸率は強度の増加によって減少するので、最終製品の特性に合わせ、これを勘案して、冷媒の温度を調節しなければならない。 On the other hand, when the reverse-transformed steel is rapidly cooled using a coolant such as ice water at room temperature (25 ° C.) or lower and maintained at room temperature, an appropriate amount of HCP martensite is generated and retained austenite at room temperature. Is to save. On the other hand, the temperature of the refrigerant during rapid cooling can be adjusted according to a desired strength level. Of course, since the stretch ratio at this time decreases with an increase in strength, the temperature of the refrigerant must be adjusted in consideration of this according to the characteristics of the final product.
以下、本発明の実施例を通して本発明をより具体的に説明する。 Hereinafter, the present invention will be described in more detail through examples of the present invention.
式１において５０〜１２０の値を満たす組成範囲の鋼を溶解して鋳造した後、熱間圧延して、鋼板を製造した。 A steel having a composition range satisfying the value of 50 to 120 in Formula 1 was melted and cast, and then hot rolled to produce a steel plate.
このように製造された熱延鋼板を利用して、幅１００ｍｍ、長さ２３０ｍｍ、厚さ１ｍｍの試片を製作した後、９５０℃に維持された焼入熱処理炉に１０分間維持した後、冷却媒（冷却油）を利用して急冷して、焼入れ熱処理した。 Using the hot-rolled steel sheet manufactured in this manner, a specimen having a width of 100 mm, a length of 230 mm, and a thickness of 1 mm was manufactured, and then maintained in a quenching heat treatment furnace maintained at 950 ° C. for 10 minutes, and then cooled. Quenching using a medium (cooling oil) and quenching heat treatment were performed.
そして、このように急冷してマルテンサイト組織を生成した後、この鋼材を再びオーステナイト逆変態開始温度（Ａｓ）以上８００℃下で焼入れした。一方、オーステナイト逆変態開始温度（Ａｓ）は、鋼の組成及び加熱速度などの影響を受けるので、実測して決定した。 And after quenching in this way and producing | generating the martensite structure | tissue, this steel material was hardened again below 800 degreeC above austenite reverse transformation start temperature (A s ). On the other hand, since the austenite reverse transformation start temperature (A s ) is affected by the composition of the steel and the heating rate, it was determined by actual measurement.
一方、本実施例においては、比較例との比較を容易にするために、７８０℃の同一な温度に維持して、２０分間再焼入れした。 On the other hand, in this example, in order to make the comparison with the comparative example easy, it was kept at the same temperature of 780 ° C. and re-quenched for 20 minutes.
表１には、本発明の実施例及び各比較例の化学組成及びＭＳ値が記載されている。
一方、このように形成された鋼を氷及び塩を混合した水で急冷（塩氷冷）した後で常温に維持して微細組織を観察し、引張実験によって物性を測定して、その結果を図１、図２、及び表２に示した。 On the other hand, the steel formed in this way is quenched with water mixed with ice and salt (salt ice cooling) and then maintained at room temperature, the microstructure is observed, the physical properties are measured by tensile experiments, and the results are obtained. This is shown in FIGS. 1 and 2 and Table 2.
図１は本発明の実施例による複合組織鋼の最終微細組織を示した写真であり、図２乃至図４は比較例１乃至３による複合組織鋼の最終微細組織を示した写真である。 FIG. 1 is a photograph showing a final microstructure of a composite steel according to an embodiment of the present invention, and FIGS. 2 to 4 are photographs showing a final microstructure of the composite steel according to Comparative Examples 1 to 3.
一方、表２には、本発明の実施例及び比較例１乃至３による複合組織鋼の引張実験の結果及び微細組織の構成が記載されている。
以下では、図１、図２、及び表２を参照して、本発明の実施例及び比較例１乃至３による複合組織鋼の差異点について説明する。 Below, with reference to FIG. 1, FIG. 2, and Table 2, the difference of the composite structure steel by the Example of this invention and Comparative Examples 1 thru | or 3 is demonstrated.
まず、比較例１の場合、多量の炭素を含むので、熱処理直後の強度は非常に高くなるが、熱処理後に常温でＢＣＴ構造のマルテンサイト単相組織に構成されるので、壊れやすい。したがって、比較例１による複合組織鋼は、延伸率及び靭性が低い。 First, in the case of Comparative Example 1, since it contains a large amount of carbon, the strength immediately after the heat treatment is very high, but it is easily broken because it is formed into a martensitic single-phase structure having a BCT structure at room temperature after the heat treatment. Therefore, the composite structure steel according to Comparative Example 1 has a low draw ratio and toughness.
次に、比較例２の場合、多量のニッケル（Ｎｉ）を利用した高合金鋼を使用して、常温で目的としたオーステナイト組織を含む。しかし、この場合、微細組織がオーステナイト単相組織に構成されていて、多量のニッケル（Ｎｉ）の添加による固溶強化効果が大きいので、他のオーステナイト単相組織に比べて強度が高いが、マルテンサイト組織が複合された相に比べては相対的に強度が低い。 Next, in the case of the comparative example 2, the high-alloy steel using a large amount of nickel (Ni) is used, and the target austenite structure is included at room temperature. However, in this case, since the microstructure is composed of an austenite single phase structure and the effect of solid solution strengthening by adding a large amount of nickel (Ni) is large, the strength is higher than that of other austenite single phase structures. The strength is relatively low compared to the phase where the site structure is combined.
また、比較例２の場合、応力が作用する時に残留オーステナイトがマルテンサイトに応力有機変態することによって延伸率が向上する鋼（実施例及び比較例３）と比較すると、延伸率がそれほど高くない。 Further, in the case of Comparative Example 2, the stretch ratio is not so high as compared with steel (Example and Comparative Example 3) in which the stretch ratio is improved by stress organic transformation of retained austenite to martensite when stress acts.
一方、比較例３の場合、適切な合金成分の含有量の選択によって、常温で目的としたオーステナイト及びマルテンサイトの複合組織を有する。 On the other hand, in the case of the comparative example 3, it has the composite structure of the austenite and martensite aimed at normal temperature by selection of content of an appropriate alloy component.
また、比較例３の強度及び延伸率をかけた値が比較例１及び２より優れている。 Further, the value obtained by multiplying the strength and the stretching ratio of Comparative Example 3 is superior to Comparative Examples 1 and 2.
しかし、比較例３のように、マンガン（Ｍｎ）の含有量が本発明の組成範囲に比べて不足したり、マンガン（Ｍｎ）以外の合金元素の含有量が本発明の組成範囲を超過する場合には、常温で存在するマルテンサイトはＢＣＣ（またはＢＣＴ）マルテンサイトであり、残留オーステナイト及びＢＣＣ（またはＢＣＴ）マルテンサイトの複合組織は、本発明の実施例のような残留オーステナイト及びＨＣＰマルテンサイトの複合組織に比べて延伸率が低い。 However, as in Comparative Example 3, the content of manganese (Mn) is insufficient compared to the composition range of the present invention, or the content of alloy elements other than manganese (Mn) exceeds the composition range of the present invention. The martensite present at room temperature is BCC (or BCT) martensite, and the composite structure of retained austenite and BCC (or BCT) martensite is the same as that of the retained austenite and HCP martensite as in the examples of the present invention. The stretch ratio is lower than that of the composite structure.
本発明の実施例によるＨＣＰマルテンサイトの場合、応力が作用する時にＢＣＣまたはＢＣＴ構造のマルテンサイトに変態するので、相対的に延伸率が高く、靭性が高いが、比較例３の場合、最初にＢＣＣ（またはＢＣＴ）構造のマルテンサイトに形成されるので、このような効果を有しにくく、本発明の実施例による効果を有することができない。 In the case of the HCP martensite according to the embodiment of the present invention, when the stress acts, it transforms into martensite having a BCC or BCT structure, so that the stretch ratio is relatively high and the toughness is high. Since it is formed in martensite having a BCC (or BCT) structure, it is difficult to have such an effect, and the effect according to the embodiment of the present invention cannot be obtained.
一方、図１を参照すれば、本発明の実施例による複合組織鋼の微細組織は、非常に微細なＴｈｉｎ Ｐｌａｔｅマルテンサイト及びオーステナイトの複合組織から構成されている。したがって、このような微細組織の構成によって、本発明の実施例による複合組織鋼は強度が高い。 On the other hand, referring to FIG. 1, the microstructure of the composite steel according to the embodiment of the present invention is composed of a very fine thin plate martensite and austenite composite structure. Therefore, the structure steel according to the embodiment of the present invention has high strength due to such a fine structure.
また、結晶粒内の相境界（Ｐｈａｓｅ ｂｏｕｎｄａｒｙ）またはマルテンサイトプレート（Ｐｌａｔｅ）内部のバリアント境界（Ｖａｒｉａｎｔ ｂｏｕｎｄａｒｙ）、双晶境界（Ｔｗｉｎ ｂｏｕｎｄａｒｙ）、積層欠陥境界（Ｓｔａｃｋｉｎｇ ｆａｕｌｔ ｂｏｕｎｄａｒｙ）などは、応力が作用する時に移動して応力エネルギーを吸収することによって、延伸率を増加させる役割を果たす。 In addition, stress acts on the phase boundary in the grain (Phase boundary), the variant boundary (Variant boundary) in the martensite plate (Plate), the twin boundary (Twin boundary), the stacking fault boundary (Stacking fault boundary), etc. It moves when it absorbs and absorbs stress energy, thereby increasing the stretch ratio.
本発明によれば、常温でオーステナイトが残留し、マルテンサイトプレートの大きさが微細で、複合組織鋼の靭性及び強度が向上する効果がある。 According to the present invention, austenite remains at room temperature, the size of the martensite plate is fine, and the toughness and strength of the composite structure steel are improved.
以上の説明は、本発明を例示的に説明したものに過ぎず、本発明が属する技術分野で通常の知識を有する者によって、本発明の本質的な特性から外れない範囲で多様な修正及び変形が可能である。また、本発明の保護範囲は特許請求の範囲によって解釈され、それと同等な範囲内にある全ての技術思想は本発明の権利範囲に含まれると解釈される。 The above description is merely illustrative of the present invention, and various modifications and variations can be made by persons having ordinary knowledge in the technical field to which the present invention belongs without departing from the essential characteristics of the present invention. Is possible. The protection scope of the present invention is construed by the claims, and all technical ideas within the scope equivalent thereto are construed as being included in the scope of the right of the present invention.
Claims (4)
ＭＳ＝２６０−３３０Ｃ＋２Ａｌ＋７Ｃｏ−１４Ｃｒ−１３Ｃｕ−１９（Ｍｎ−１５）−５Ｍｏ−４Ｎｂ−１３Ｎｉ−７Ｓｉ＋３Ｔｉ−４Ｖ
において５０乃至１２０の値を満たす鋼を熱間圧延して、鋼材を製造する段階；
前記鋼材を加熱して焼入れして、マルテンサイト組織を含むように急冷する１次焼入段階；
前記１次焼入段階で焼き入れされた鋼材を、オーステナイト逆変態開始温度（Ａｓ）以上８００℃以下の範囲で加熱した後で焼入れして、逆変態されたオーステナイト結晶粒の大きさを微細化する２次焼入段階；
前記２次焼入段階後に前記鋼材を急冷して、ＨＣＰマルテンサイトを生成する急冷段階；及び
前記急冷段階後に前記鋼材を常温に維持して、残留オーステナイトを保存する段階；
を含む、複合組織鋼を提供するための熱処理方法。 In mass percent basis, C: 0. 5 or less, Mn: more than 15 and 35 or less, total of any one of Co, Ti, and Al : 3 or less, any of Cr, Cu, Mo, Ni, Nb, Si, and V Total of one or more: 10 or less, the remainder consists of Fe and other impurities that are unavoidably added, and the content of the alloy component is represented by the following MS formula:
MS = 260-330C + 2Al + 7Co-14Cr-13Cu-19 (Mn-15) -5Mo-4Nb-13Ni-7Si + 3Ti-4V
Hot-rolling steel satisfying a value of 50 to 120 in step to produce a steel material;
A primary quenching step of heating and quenching the steel material and quenching to include a martensite structure;
The steel material quenched in the primary quenching step is heated in the range of the austenite reverse transformation start temperature (A s ) to 800 ° C. and then quenched to finely reduce the size of the reverse-transformed austenite crystal grains. Secondary quenching stage to be converted;
A quenching step of quenching the steel after the secondary quenching step to produce HCP martensite ; and
Maintaining the steel at room temperature after the quenching step to store residual austenite;
Heat treatment method for including, providing a composite structure steel.
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| US10597742B2 (en) | 2014-08-14 | 2020-03-24 | Yanshan University | Low-temperature high-strength-and-ductility high manganese steel, and high manganese steel plate and high manganese steel tube manufacturing process |
| KR101657808B1 (en) * | 2014-12-22 | 2016-09-20 | 주식회사 포스코 | Austenitic steel with excellent resistance for adiabatic shear band formability and method for manufacturing thereof |
| KR101736636B1 (en) * | 2015-12-23 | 2017-05-17 | 주식회사 포스코 | HIHG-Mn STEEL PLATE HAVING EXCELLENT DAMPING PROPERTY AND METHOD FOR PRODUCING THE SAME |
| KR101736637B1 (en) * | 2015-12-23 | 2017-05-17 | 주식회사 포스코 | HIHG-Mn STEEL PLATE HAVING EXCELLENT DAMPING PROPERTY AND METHOD FOR PRODUCING THE SAME |
| CN107190201B (en) * | 2017-07-17 | 2019-03-26 | 武汉钢铁有限公司 | LPG ship steel and manufacturing method |
| KR102276740B1 (en) | 2018-12-18 | 2021-07-13 | 주식회사 포스코 | High strength steel sheet having excellent ductility and workability, and method for manufacturing the same |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR890002033B1 (en) * | 1985-08-31 | 1989-06-08 | 한국과학기술원 | Steel alloy for super low temperature and the producing method |
| JPH02104633A (en) * | 1989-07-28 | 1990-04-17 | Daido Steel Co Ltd | High strength non-magnetic high manganese steel |
| DE69226946T2 (en) * | 1991-12-30 | 1999-05-12 | Pohang Iron & Steel Co. Ltd., Pohang City, Kyung Sang Book | AUSTENITIC MANGANIC STEEL SHEET WITH HIGH DEFORMABILITY, STRENGTH AND WELDABILITY AND METHOD |
| KR960006453B1 (en) * | 1993-10-22 | 1996-05-16 | 최종술 | Fe-Mn vibration damping alloy steel and its manufacturing method |
| KR970001324B1 (en) * | 1994-03-25 | 1997-02-05 | 김만제 | Hot rolling method of high mn steel |
| JP3787224B2 (en) * | 1996-08-29 | 2006-06-21 | 株式会社大東製作所 | Sliding shaft member and non-magnetic shaft member |
| JP3379355B2 (en) * | 1996-10-21 | 2003-02-24 | 住友金属工業株式会社 | High-strength steel used in an environment requiring sulfide stress cracking resistance and method of manufacturing the same |
| JP4529872B2 (en) * | 2005-11-04 | 2010-08-25 | 住友金属工業株式会社 | High Mn steel material and manufacturing method thereof |
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| KR100840287B1 (en) | 2008-06-20 |
| JP2010511790A (en) | 2010-04-15 |
| CN101568660A (en) | 2009-10-28 |
| WO2008078962A1 (en) | 2008-07-03 |
| CN101568660B (en) | 2012-11-28 |
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