JP2005133180A - Steel sheet for heat treatment, and its production method - Google Patents
Steel sheet for heat treatment, and its production method Download PDFInfo
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- JP2005133180A JP2005133180A JP2003372910A JP2003372910A JP2005133180A JP 2005133180 A JP2005133180 A JP 2005133180A JP 2003372910 A JP2003372910 A JP 2003372910A JP 2003372910 A JP2003372910 A JP 2003372910A JP 2005133180 A JP2005133180 A JP 2005133180A
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 102
- 239000010959 steel Substances 0.000 title claims abstract description 102
- 238000010438 heat treatment Methods 0.000 title claims abstract description 25
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 14
- 238000004140 cleaning Methods 0.000 claims abstract description 20
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims abstract description 15
- 229910000604 Ferrochrome Inorganic materials 0.000 claims abstract description 12
- 239000002344 surface layer Substances 0.000 claims abstract description 10
- 230000003746 surface roughness Effects 0.000 claims abstract description 7
- 239000003513 alkali Substances 0.000 claims abstract description 5
- 238000007731 hot pressing Methods 0.000 claims description 12
- 229910004283 SiO 4 Inorganic materials 0.000 claims description 11
- 239000000203 mixture Substances 0.000 claims description 8
- 229910052804 chromium Inorganic materials 0.000 claims description 7
- 238000000465 moulding Methods 0.000 claims description 7
- 239000000126 substance Substances 0.000 claims description 7
- 239000010410 layer Substances 0.000 claims description 4
- 230000003647 oxidation Effects 0.000 abstract description 17
- 238000007254 oxidation reaction Methods 0.000 abstract description 17
- 238000005554 pickling Methods 0.000 abstract description 9
- 238000011282 treatment Methods 0.000 abstract description 6
- 238000005406 washing Methods 0.000 abstract description 5
- 239000010960 cold rolled steel Substances 0.000 abstract description 3
- 239000002585 base Substances 0.000 abstract description 2
- UQSXHKLRYXJYBZ-UHFFFAOYSA-N Iron oxide Chemical compound [Fe]=O UQSXHKLRYXJYBZ-UHFFFAOYSA-N 0.000 description 50
- 230000000694 effects Effects 0.000 description 19
- 238000010791 quenching Methods 0.000 description 16
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 15
- 230000000171 quenching effect Effects 0.000 description 14
- 238000001816 cooling Methods 0.000 description 8
- 230000001965 increasing effect Effects 0.000 description 8
- 239000000463 material Substances 0.000 description 8
- 238000000034 method Methods 0.000 description 8
- 229910001566 austenite Inorganic materials 0.000 description 7
- 238000005097 cold rolling Methods 0.000 description 7
- QAOWNCQODCNURD-UHFFFAOYSA-N Sulfuric acid Chemical compound OS(O)(=O)=O QAOWNCQODCNURD-UHFFFAOYSA-N 0.000 description 6
- 238000005098 hot rolling Methods 0.000 description 6
- 229920006395 saturated elastomer Polymers 0.000 description 6
- VEXZGXHMUGYJMC-UHFFFAOYSA-N Hydrochloric acid Chemical compound Cl VEXZGXHMUGYJMC-UHFFFAOYSA-N 0.000 description 4
- 239000004677 Nylon Substances 0.000 description 4
- 230000002708 enhancing effect Effects 0.000 description 4
- 230000002401 inhibitory effect Effects 0.000 description 4
- 229920001778 nylon Polymers 0.000 description 4
- 239000002436 steel type Substances 0.000 description 4
- 229910045601 alloy Inorganic materials 0.000 description 3
- 239000000956 alloy Substances 0.000 description 3
- 239000007864 aqueous solution Substances 0.000 description 3
- 238000007796 conventional method Methods 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 230000007797 corrosion Effects 0.000 description 3
- 238000011156 evaluation Methods 0.000 description 3
- 229910000734 martensite Inorganic materials 0.000 description 3
- 239000002253 acid Substances 0.000 description 2
- 238000005422 blasting Methods 0.000 description 2
- 239000011248 coating agent Substances 0.000 description 2
- 238000000576 coating method Methods 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 239000003112 inhibitor Substances 0.000 description 2
- 239000007788 liquid Substances 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 230000001590 oxidative effect Effects 0.000 description 2
- 238000003825 pressing Methods 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 239000000523 sample Substances 0.000 description 2
- 239000000758 substrate Substances 0.000 description 2
- 230000001629 suppression Effects 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000011109 contamination Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 238000005238 degreasing Methods 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 229910052737 gold Inorganic materials 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 1
- 239000011259 mixed solution Substances 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 238000006386 neutralization reaction Methods 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 150000004965 peroxy acids Chemical class 0.000 description 1
- 230000002265 prevention Effects 0.000 description 1
- 230000003014 reinforcing effect Effects 0.000 description 1
- 238000012827 research and development Methods 0.000 description 1
- 238000000926 separation method Methods 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- POWFTOSLLWLEBN-UHFFFAOYSA-N tetrasodium;silicate Chemical compound [Na+].[Na+].[Na+].[Na+].[O-][Si]([O-])([O-])[O-] POWFTOSLLWLEBN-UHFFFAOYSA-N 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
- 238000004804 winding Methods 0.000 description 1
Landscapes
- Heat Treatment Of Sheet Steel (AREA)
- Cleaning And De-Greasing Of Metallic Materials By Chemical Methods (AREA)
Abstract
Description
本発明は、自動車のボデー構造部品、足回り部品等を初めとする機械構造部品等の製造に使用される熱処理用鋼材とその製造方法に関する。 The present invention relates to a steel material for heat treatment used in the manufacture of machine structural parts such as automobile body structural parts and undercarriage parts, and a method for producing the same.
近年、自動車の軽量化のため、鋼材の高強度化を図り、使用重量を減ずる努力が進んでいる。自動車に広く使用される薄鋼板においては、鋼板強度の増加に伴って、プレス成形性が低下し、複雑な形状を製造することが困難になってきている。具体的には、延性が低下し加工度が高い部位で破断が生じる、あるいはスプリングバックや壁反りが大きくなり寸法精度が劣化するという問題が発生する。従って、高強度、特に780MPa級以上の鋼板を用いて、プレス成形で部品を製造することは容易ではない。プレス成形ではなくロール成形によれば、高強度の鋼板の加工が可能であるが、長手方向に一様な断面を有する部品にしか適用できない。 In recent years, in order to reduce the weight of automobiles, efforts have been made to increase the strength of steel materials and reduce the weight used. In thin steel plates widely used in automobiles, press formability decreases with increasing steel plate strength, making it difficult to manufacture complex shapes. Specifically, there arises a problem that fracture occurs at a site where ductility is reduced and the degree of processing is high, or a springback or wall warp becomes large and dimensional accuracy deteriorates. Therefore, it is not easy to produce parts by press molding using a steel plate having high strength, particularly 780 MPa class or higher. According to roll forming instead of press forming, it is possible to process a high-strength steel sheet, but it can be applied only to parts having a uniform cross section in the longitudinal direction.
一方、特許文献1に示されているように、加熱した鋼板をプレス成形する熱間プレスと呼ばれる方法によれば、鋼板が高温で軟質、高延性になっているため、複雑な形状を寸法精度よく成形することが可能である。さらに、鋼板をオーステナイト域に加熱しておき、金型内で急冷することにより、マルテンサイト変態による鋼板の高強度化が同時に達成できるとしている。 On the other hand, as shown in Patent Document 1, according to a method called hot press that press-forms a heated steel plate, the steel plate is soft and highly ductile at high temperatures, so that a complicated shape has a dimensional accuracy. It is possible to mold well. Furthermore, the steel sheet is heated in the austenite region and rapidly cooled in the mold, so that it is possible to simultaneously achieve high strength of the steel sheet by martensitic transformation.
また、特許文献2では、室温で予め所定の形状に成形後、オーステナイト域に加熱し、金型内で急冷することで鋼板の高強度化と成形性の確保とを同時に達成する予プレスクエンチ法が開示されている。 Further, in Patent Document 2, a pre-press quench method that simultaneously achieves high strength of the steel sheet and securing of formability by heating to an austenite region and rapidly cooling in a mold after forming into a predetermined shape at room temperature. Is disclosed.
このような熱間プレス法や予プレスクエンチ法は、部材の高強度化と成形性を同時に確保できる優れた成形方法であるが、800〜1000℃といった高温に加熱することが必要なため、鋼板表面が酸化するという問題が生じる。このときの加熱により生じた鉄酸化物からなるスケールがプレス時に脱落して金型に付着して生産性が低下したり、あるいはプレス後の製品にそのようなスケールが残存して外観が不良となるという問題がある。しかも、このようなスケールが残存すると、次工程で塗装する場合に鋼板と塗膜の密着性が劣り、耐食性の低下を招く。そこでプレス成形後は、ショットブラスト等のスケール除去処理が必要となる。 Such hot press method and pre-press quench method are excellent forming methods that can ensure high strength and formability at the same time, but they need to be heated to a high temperature of 800-1000 ° C. The problem arises that the surface is oxidized. The scale composed of iron oxide generated by heating at this time falls off during pressing and adheres to the mold, resulting in reduced productivity, or such scale remains in the product after pressing and the appearance is poor. There is a problem of becoming. In addition, if such a scale remains, the adhesion between the steel sheet and the coating film is inferior when coating is performed in the next step, leading to a decrease in corrosion resistance. Therefore, after press molding, a scale removal process such as shot blasting is required.
従って、生成するスケールに要求される特性としては、プレス時には剥離脱落して金型汚染を引き起こすことなく、ショットブラスト処理時には容易に剥離除去されやすいことである。 Therefore, a characteristic required for the scale to be produced is that it is easily peeled and removed during shot blasting without causing separation and dropping during press to cause mold contamination.
例えば、通常の熱間プレス前の加熱では、スケール生成を抑制するため非酸化性雰囲気(例えばガス炉−空燃比0.9)での加熱が行われることが多い。それでも通常の鋼板では、スケール生成量が多く、熱間プレス時にそのようなスケールは剥離しやすく金型を汚染することが問題となっている。 For example, in normal heating before hot pressing, heating in a non-oxidizing atmosphere (for example, a gas furnace-air-fuel ratio 0.9) is often performed in order to suppress scale formation. Nevertheless, a normal steel plate has a large amount of scale generation, and such a scale is easily peeled off during hot pressing, and the mold is contaminated.
本発明の課題は、熱処理後あるいは熱間プレス後の最終製品部材の表層に生成するスケール量が少なくなる熱処理用鋼板とその製造方法を提供することである。 An object of the present invention is to provide a steel plate for heat treatment that reduces the amount of scale generated on the surface layer of the final product member after heat treatment or after hot pressing, and a method for producing the same.
本発明者らは、熱処理後あるいは熱間プレス後に部材の表層に生成するスケール量が少なくなるよう鋭意検討した結果、鋼中のSi量およびCr量、さらに好ましくは鋼板表面粗さを一定範囲内に収め、かつ特別な洗浄を施すことで、鋼板の酸化が抑制されることを見いだした。 As a result of diligent study to reduce the amount of scale formed on the surface layer of the member after heat treatment or after hot pressing, the present inventors have determined that the amount of Si and Cr in steel, and more preferably, the steel sheet surface roughness is within a certain range. In addition, it was found that oxidation of the steel sheet is suppressed by performing special cleaning.
また、そのような鋼板は、大気酸化させた場合に特別なスケール構造となって更なる酸化が抑制されることが判明した。そして、その後の研究開発により、最もスケールが生成しやすい大気酸化においてこのようなスケール構造となる鋼板は、その後、多くの酸化雰囲気下に置かれても、本質的に酸化されがたいことを見いだした。 Further, it has been found that such a steel sheet has a special scale structure when it is oxidized in the atmosphere, and further oxidation is suppressed. Then, through subsequent research and development, it was found that steel plates that have such a scale structure in atmospheric oxidation, which is most likely to generate scale, are essentially difficult to oxidize even when placed in many oxidizing atmospheres. It was.
その知見に基づき完成させた本発明は、次の通りである。
(1)質量%で、Si:0.01〜0.5%、Cr:0.01〜0.5%を含有する化学組成を有する鋼板であって、その鋼板を大気中でAC3点以上に加熱保持後、急冷焼入れ処理を行った後に表層に生成するスケールが、鋼板との界面にFeO、FeCr2O4、およびFe2SiO4の混合相、その上が実質上FeOの単相となる熱処理用鋼板。
The present invention completed based on the knowledge is as follows.
(1) A steel sheet having a chemical composition containing Si: 0.01 to 0.5% and Cr: 0.01 to 0.5% by mass%, and the steel sheet is heated and held above the AC3 point in the atmosphere and then quenched and quenched. A steel sheet for heat treatment in which the scale formed on the surface layer after the heat treatment is a mixed phase of FeO, FeCr 2 O 4 , and Fe 2 SiO 4 at the interface with the steel sheet, and the upper layer is substantially a single phase of FeO.
(2)質量%で、Si:0.01〜0.5%、Cr:0.01〜0.5%を含有する化学組成を有する鋼板であって、その鋼板を大気中でAC3点以上に加熱保持後、成形用金型を用いてプレス成形を行った後に表層に生成するスケールが、鋼板との界面にFeO、FeCr2O4、およびFe2SiO4の混合相、その上が実質上FeOの単相となる熱間プレス用鋼板。 (2) A steel plate having a chemical composition containing Si: 0.01 to 0.5% and Cr: 0.01 to 0.5% by mass%, and after heating and holding the steel plate to the AC3 point or higher in the atmosphere, the forming gold The scale that forms on the surface layer after press molding using a mold is a heat that is a mixed phase of FeO, FeCr 2 O 4 , and Fe 2 SiO 4 at the interface with the steel plate, and a substantially single phase of FeO above it. Steel sheet for hot pressing.
(3)鋼板表面平均粗さが3.0μm以下である上記(1)または(2)に記載の鋼板。
(4)熱間圧延および酸洗を行った鋼板であって、あるいはさらに冷間圧延を行った鋼板であって、表面平均粗さが3.0μm以下である鋼板表面にブラシ水洗浄を行い、その後、酸洗を行い、さらにアルカリ洗浄を行い、最後にブラシ水洗浄を行うことを特徴とする上記(1)ないし(3)のいずれかに記載の鋼板の製造方法。
(3) The steel sheet according to (1) or (2), wherein the steel sheet has an average surface roughness of 3.0 μm or less.
(4) A steel sheet that has been hot-rolled and pickled, or a steel sheet that has been further cold-rolled, and is subjected to brush water cleaning on the steel sheet surface having a surface average roughness of 3.0 μm or less, and then The method for producing a steel sheet according to any one of (1) to (3) above, wherein pickling is performed, alkali cleaning is performed, and brush water cleaning is finally performed.
さらに別の面からは、本発明は、表層に生成するスケールが、鋼板との界面にFeO、FeCr2O4、およびFe2SiO4の混合相、その上が実質上FeOの単相となる構成を備えた熱処理鋼材もしくは熱間プレス鋼材である。 From another aspect, the present invention provides a scale formed on the surface layer of a mixed phase of FeO, FeCr 2 O 4 , and Fe 2 SiO 4 at the interface with the steel plate, and a substantially single phase of FeO thereon. It is a heat-treated steel material or a hot-pressed steel material having a structure.
本発明により、熱処理後あるいは熱間プレス後、部材の表層に生成するスケール量が少なくなる熱処理用鋼板あるいは熱間プレス用鋼板とその製造方法を提供することが可能となる。 According to the present invention, it is possible to provide a steel plate for heat treatment or a steel plate for hot pressing in which the amount of scale generated on the surface layer of the member is reduced after heat treatment or after hot pressing, and a manufacturing method thereof.
次に、本発明において、各範囲に限定した理由について説明する。なお、本明細書において、特にことわりがない限り、鋼の化学組成を規定する「%」は「質量%」を表す。 Next, the reason why the present invention is limited to each range will be described. In the present specification, unless otherwise specified, “%” defining the chemical composition of steel represents “mass%”.
1.鋼板成分について
鋼板の化学組成については、以下のように規定する。
Si:0.01〜0.5%
Siは、酸化抑制効果を有するFe2SiO4 を生成する元素である。しかしSi含有量が0.01%未満ではその効果は十分ではなく、一方でSi含有量が0.5%を超えるとその効果は飽和し、いたずらにコスト増を招く。より望ましいSi含有量は、0.05〜0.30%である。さらに望ましくは0.10〜0.30%である。
1. Steel plate components The chemical composition of steel plates is specified as follows.
Si: 0.01-0.5%
Si is an element that generates Fe 2 SiO 4 having an oxidation suppressing effect. However, when the Si content is less than 0.01%, the effect is not sufficient. On the other hand, when the Si content exceeds 0.5%, the effect is saturated, and the cost is unnecessarily increased. A more desirable Si content is 0.05 to 0.30%. More desirably, it is 0.10 to 0.30%.
Cr:0.01〜0.5%
Crは、酸化抑制効果を有するFeCr2O4を生成する元素である。しかしCr含有量が0.01%未満ではその効果は十分ではなく、一方でCr含有量が0.5%をこえるとその効果は飽和し、いたずらにコスト増を招く。より望ましいCr含有量は、0.15〜0.30%である。
Cr: 0.01-0.5%
Cr is an element that generates FeCr 2 O 4 having an oxidation inhibiting effect. However, if the Cr content is less than 0.01%, the effect is not sufficient. On the other hand, if the Cr content exceeds 0.5%, the effect is saturated, and the cost is unnecessarily increased. A more desirable Cr content is 0.15 to 0.30%.
その他の合金元素については特に限定はしないが、例えば自動車用補強部材のような用途におけるように焼入れ後の980MPa 以上の強度確保のため、通常、含有される各合金元素について、望ましい成分範囲について述べる。なお、焼入れ後の強度確保が不要な場合、例えば、高温での軟質状態を成形目的で利用する場合には、次の限定をする必要はない。 Other alloy elements are not particularly limited. For example, in order to secure a strength of 980 MPa or more after quenching as in an application such as an automotive reinforcing member, a desirable component range is usually described for each alloy element contained. . In addition, when it is not necessary to ensure strength after quenching, for example, when a soft state at a high temperature is used for molding purposes, the following limitation is not necessary.
C:0.15〜0.45%
Cは、鋼板の焼入れ性を高めかつ焼入れ後の強度を主に決定する非常に重要な元素である。さらにAC3点を下げ、焼入れ処理温度の低温化を促進する元素である。しかしC含有量が0.15%未満では、その効果は十分ではなく、一方でC含有量が0.45%を超えると焼入れ部の靱性劣化が著しくなる。より望ましいC含有量は0.16〜0.35%である。
C: 0.15-0.45%
C is a very important element that enhances the hardenability of the steel sheet and mainly determines the strength after quenching. Further lowering the C3 point A, it is an element which promotes lowering the quenching temperature. However, if the C content is less than 0.15%, the effect is not sufficient. On the other hand, if the C content exceeds 0.45%, the toughness of the quenched portion becomes significantly deteriorated. A more desirable C content is 0.16 to 0.35%.
Mn:0.5〜3.0%
Mnは、鋼板の焼入れ性を高めかつ焼入れ後の強度を安定して確保するために、非常に効果のある元素である。さらにAC3点を下げ、焼入れ処理温度の低温化を促進する元素である。しかしMn含有量が0.5%未満ではその効果は十分ではなく、一方でMn含有量が3.0%を超えるとその効果は飽和し、さらに焼入れ部の靱性劣化を招く。より望ましいMn含有量は0.8〜2.0%である。
Mn: 0.5-3.0%
Mn is an element that is very effective for enhancing the hardenability of the steel sheet and stably securing the strength after quenching. Further lowering the C3 point A, it is an element which promotes lowering the quenching temperature. However, if the Mn content is less than 0.5%, the effect is not sufficient. On the other hand, if the Mn content exceeds 3.0%, the effect is saturated, and further, the toughness of the quenched portion is deteriorated. A more desirable Mn content is 0.8 to 2.0%.
Cr:0.1〜0.5%
Crは、鋼板の焼入れ性を高めかつ焼入れ後強度を安定して確保するために効果のある元素である。しかし、そのような目的にはCr含有量が0.1%未満ではその効果は十分ではなく、一方でCr含有量が0.5%をこえるとその効果は飽和し、いたずらにコスト増を招く。より望ましいCr含有量は、0.15〜0.30%である。
Cr: 0.1-0.5%
Cr is an element that is effective for enhancing the hardenability of the steel sheet and stably securing the strength after quenching. However, if the Cr content is less than 0.1% for such purposes, the effect is not sufficient. On the other hand, if the Cr content exceeds 0.5%, the effect is saturated and the cost is unnecessarily increased. A more desirable Cr content is 0.15 to 0.30%.
Ti:0.01〜0.1%
Tiは、鋼板の焼入れ性を高めかつ焼入れ後強度を安定して確保するために効果のある元素である。さらに焼入れ部の靱性も向上させる効果を有する。しかしTi含有量が0.01%未満ではその効果は十分ではなく、一方でTi含有量が0.1%をこえるとその効果は飽和し、いたずらにコスト増を招く。より望ましいTi含有量は0.015〜0.03%である。
Ti: 0.01-0.1%
Ti is an element effective for enhancing the hardenability of the steel sheet and stably securing the strength after quenching. Furthermore, it has the effect of improving the toughness of the quenched portion. However, if the Ti content is less than 0.01%, the effect is not sufficient. On the other hand, if the Ti content exceeds 0.1%, the effect is saturated, and the cost is increased. A more desirable Ti content is 0.015 to 0.03%.
B:0.0002〜0.004%
Bは、鋼板の焼入れ性を高めかつ焼入れ後強度の安定確保効果をさらに高める重要な元素である。しかしB含有量が0.0002%未満ではその効果は十分ではなく、一方でB含有量が0.004%を超えるとその効果は飽和し、かつコスト増を招く。より望ましいB含有量は0.0005〜0.0025%である。
B: 0.0002 to 0.004%
B is an important element that enhances the hardenability of the steel sheet and further enhances the effect of ensuring the stability of the strength after quenching. However, if the B content is less than 0.0002%, the effect is not sufficient. On the other hand, if the B content exceeds 0.004%, the effect is saturated and the cost is increased. A more desirable B content is 0.0005 to 0.0025%.
P:0.05%以下、S:0.05%以下、Ni:2%以下、Cu:1%以下、Mo:1%以下、V:1%以下、Nb:1%以下、Al:1%以下、N:0.01%以下
これらの元素も、鋼板の焼入れ性を高めかつ焼入れ後強度の安定確保に効果の有る元素である。所望により、少なくとも1種配合される。しかしそれぞれ上限値を超えて含有させてもその効果は小さく、かついたずらにコスト増を招くため、各合金元素の含有量は上述の範囲が望ましい。
P: 0.05% or less, S: 0.05% or less, Ni: 2% or less, Cu: 1% or less, Mo: 1% or less, V: 1% or less, Nb: 1% or less, Al: 1% or less, N: 0.01% or less These elements are also elements that are effective in enhancing the hardenability of the steel sheet and ensuring the stability of the strength after quenching. If desired, at least one compound is blended. However, even if each content exceeds the upper limit, the effect is small and the cost is unnecessarily increased. Therefore, the content of each alloy element is preferably within the above range.
2.加熱条件、保持時間および冷却速度について
焼入れ処理を行うためには、まず鋼板をオーステナイト温度域まで加熱し、全面を一度、オーステナイト相にする必要がある。そのためにはAC3点以上に加熱し、その温度で1分以上保持するのが望ましい。保持時間の上限は特には設けないが、実生産上の効率を考えて、上限を保持時間10分にするのが望ましい。
2. In order to quench the heating conditions, holding time, and cooling rate, it is necessary to first heat the steel sheet to the austenite temperature range and to once convert the entire surface into the austenite phase. For this purpose, it is desirable to heat to AC 3 point or higher and hold at that temperature for 1 minute or longer. The upper limit of the holding time is not particularly set, but it is desirable to set the upper limit to 10 minutes in consideration of the efficiency in actual production.
このときの加熱温度および保持時間とそれにより生成する酸化スケールの構成との関係は次の通りである。
まず大気酸化時では界面に、FeO、FeCr2O4、Fe2SiO4が形成されている。その混合相がある程度の厚さ(数μm以下)になった後、その混合相の上方にFeO単相が形成されていくが、最外層には、一部、Fe3O4やFe2O3も形成される。
The relationship between the heating temperature and holding time at this time, and the structure of the oxide scale produced | generated by it is as follows.
First, during atmospheric oxidation, FeO, FeCr 2 O 4, and Fe 2 SiO 4 are formed at the interface. After the mixed phase has reached a certain thickness (several μm or less), a FeO single phase is formed above the mixed phase, but in the outermost layer, a part of Fe 3 O 4 or Fe 2 O is formed. 3 is also formed.
冷却速度については、熱処理後にマルテンサイト組織を得るため、その鋼の臨界冷却速度以上の冷却速度を確保してやればよい。いわゆる急冷焼入れである。
このときの冷却停止温度は、特に制限はなく、室温にまで冷却してもよいが、本発明の場合には、そのような冷却によって焼入れ効果ばかりでなく、目的とする酸化スケールの生成を意図することから、それを実現できればいずれの温度にまで冷却してもよい。のぞましくはこのときの冷却停止温度は、100℃である。
About a cooling rate, in order to obtain a martensitic structure after heat processing, what is necessary is just to ensure the cooling rate more than the critical cooling rate of the steel. This is so-called quenching and quenching.
The cooling stop temperature at this time is not particularly limited, and may be cooled to room temperature. However, in the case of the present invention, not only the quenching effect but also the generation of the target oxide scale is intended by such cooling. Therefore, if it can be realized, it may be cooled to any temperature. Preferably, the cooling stop temperature at this time is 100 ° C.
本発明の別の態様によれば、上記急冷焼入れに代えて、成形用金型を用いて熱間プレス成形を行ってもよい。 According to another aspect of the present invention, hot press molding may be performed using a molding die instead of the rapid quenching.
3.鋼板の製造方法について
本発明にかかる鋼板は、その使用に先立って、一旦、オーステナイト域またはオーステナイト域近傍に加熱される。従って、加熱前の室温での機械的性質は重要ではなく、加熱前の金属組織については特に規定しない。つまり、鋼板として熱延鋼板または冷延鋼板のいずれを使用してもよく、その製造方法については限定しない。しかし、生産性の観点から、好適な製造方法を以下に述べる。
3. About the manufacturing method of a steel plate The steel plate concerning this invention is once heated to the austenite area | region or the austenite area vicinity before the use. Therefore, the mechanical properties at room temperature before heating are not important, and the metal structure before heating is not particularly specified. That is, either a hot-rolled steel plate or a cold-rolled steel plate may be used as the steel plate, and the manufacturing method is not limited. However, from the viewpoint of productivity, a preferable manufacturing method is described below.
熱間圧延:熱間圧延は、常法によって行えばよいが、圧延の安定性の観点から、オーステナイト域で行うことが好ましい。熱間圧延後は、巻取温度を規定するのが好ましいが、巻取温度が低いと、マルテンサイト組織となって強度が上昇し、冷間圧延が困難になる。一方、巻取温度が高いと、酸化スケールが厚くなり、引き続き行う酸洗の効率が低下する。従って巻取温度は、500〜600℃が好ましい。このようにして得られた熱間圧延材には酸洗を行うが、そのときの酸洗では、塩酸水溶液または硫酸水溶液を用いて、熱間圧延時に生成したスケールを除去する。通常、酸濃度は高々、塩酸で3〜10%、硫酸で15〜25%程度であり、液温度は通常、80〜100℃程度である。また過酸洗状態(地鉄の溶解)を防ぐため、ごく少量の酸洗抑制剤を添加してもよい。この抑制剤は地鉄表面に膜をつくり、この膜が地鉄の酸による腐食を防ぐ。 Hot rolling: Hot rolling may be performed by a conventional method, but is preferably performed in the austenite region from the viewpoint of rolling stability. After the hot rolling, it is preferable to define the coiling temperature. However, if the coiling temperature is low, a martensite structure is formed, the strength is increased, and cold rolling becomes difficult. On the other hand, if the coiling temperature is high, the oxide scale becomes thick and the efficiency of the subsequent pickling is reduced. Accordingly, the winding temperature is preferably 500 to 600 ° C. The hot-rolled material thus obtained is pickled. In pickling at that time, a hydrochloric acid aqueous solution or a sulfuric acid aqueous solution is used to remove scales produced during hot rolling. Usually, the acid concentration is at most about 3 to 10% with hydrochloric acid and about 15 to 25% with sulfuric acid, and the liquid temperature is usually about 80 to 100 ° C. Further, a very small amount of pickling inhibitor may be added in order to prevent a per-acid wash state (dissolution of the base iron). This inhibitor forms a film on the surface of the steel, which prevents corrosion of the steel by acid.
冷間圧延:冷間圧延は、常法によって行う。本発明の鋼板は、通常は炭素含有量が高い場合が多く、過度の圧下率で冷間圧延するとミルの負担が大きくなる。また、加工硬化により冷間圧延後の強度が高くなりすぎると、コイル接続時の溶接強度やライン通板能力が問題となる。従って圧下率は80%以下が好ましく、70%以下がさらに好ましい。 Cold rolling: Cold rolling is performed by a conventional method. The steel sheet of the present invention usually has a high carbon content in many cases, and if it is cold-rolled at an excessive reduction rate, the burden on the mill increases. In addition, if the strength after cold rolling becomes too high due to work hardening, the welding strength and line passing ability at the time of coil connection become a problem. Accordingly, the rolling reduction is preferably 80% or less, and more preferably 70% or less.
なお、冷間圧延はコスト増となるので、熱間圧延で製造可能な板厚、板幅の鋼板については、冷間圧延を省略し、熱間圧延−酸洗ままの鋼板を用いるのが好ましい。 In addition, since cold rolling increases the cost, it is preferable to omit the cold rolling and use a hot-rolled and pickled steel plate for a steel plate having a thickness and width that can be manufactured by hot rolling. .
4.鋼板の洗浄方法、表面粗さ及び生成スケールについて
前述のようにして得られた熱延鋼板あるいは冷延鋼板であって、鋼板表面平均粗さ3.0μm以下なる鋼板にブラシ水洗浄−酸洗−アルカリ洗浄−ブラシ水洗浄の一連の処理を施すと、詳細なメカニズムは不明であるが、鋼板に酸化抑制効果が付与される。ただし、鋼板表面平均粗さが3.0μmを超えると酸化抑制効果が不十分となる。より好ましい表面平均粗さは0.3〜1μmである。
4. Hot-rolled or cold-rolled steel sheet obtained as described above with respect to the steel sheet cleaning method, surface roughness, and production scale, and steel sheet with an average surface roughness of 3.0 μm or less. -When a series of treatments of alkali cleaning and brush water cleaning are performed, the detailed mechanism is unknown, but an oxidation suppressing effect is imparted to the steel sheet. However, when the steel sheet surface average roughness exceeds 3.0 μm, the oxidation suppressing effect becomes insufficient. A more preferable surface average roughness is 0.3 to 1 μm.
ここに、「ブラシ水洗浄」は、例えばナイロンブラシを使って1〜10秒間行う水洗浄であり、これは最初の水洗浄は表面の軽洗浄のために、最後の水洗浄はアルカリ液除去 のために行う。金属ブラシは表面粗が拡大するので好ましくない。また「酸洗」、「アルカリ洗浄」も慣用のものであればよく、特にアルカリ洗浄は酸洗後の中和および脱脂を行うためである。 Here, “brush water cleaning” is, for example, water cleaning performed using a nylon brush for 1 to 10 seconds. This is because the first water cleaning is for light cleaning of the surface, and the last water cleaning is for removing alkaline liquid. To do. A metal brush is not preferable because the surface roughness increases. Further, “pickling” and “alkaline washing” may be conventional ones, and the alkali washing is particularly for neutralization and degreasing after pickling.
このような洗浄処理を行った鋼板を大気酸化させた場合、酸化されにくいため、FeO、FeCr2O4、Fe2SiO4が鋼板界面に均一に形成し、これらのスケールによってさらに酸化抑制効果が発現し、そのため混合相上に形成されるスケールが実質上FeOの単相、つまり「実質FeO単相」となる。ここでいう、「実質FeO単相」とは、混合相上に形成されるスケール中のFeO体積率が98%以上になることを指す。 When a steel plate subjected to such cleaning treatment is oxidized in the atmosphere, it is difficult to oxidize, so FeO, FeCr 2 O 4 , and Fe 2 SiO 4 are uniformly formed at the steel plate interface. Therefore, the scale formed on the mixed phase is substantially a single phase of FeO, that is, “substantially FeO single phase”. As used herein, “substantially FeO single phase” means that the FeO volume fraction in the scale formed on the mixed phase is 98% or more.
なお、かかる混合相と実質FeO単相との区別は、X線回折装置による分析や電子プローブマイクロアナライザーによる分析によって行い、これらの相は2相に分化しているので、 通常の光学顕微鏡(ナイタール腐食)観察によって明瞭に区別される。 The mixed phase and the actual FeO single phase are distinguished by analysis using an X-ray diffractometer or an electron probe microanalyzer, and these phases are differentiated into two phases. Corrosion) is clearly distinguished by observation.
SiやCrを含有する通常の鋼板を大気酸化させた場合でも、基板との界面にFeO、FeCr2O4、Fe2SiO4の混合相が出来る。しかしながら、通常の鋼板は、酸化されやすいため、FeCr2O4、Fe2SiO4が不均一に形成し、その酸化抑制効果が十分には発揮されず、そのため、混合相上に形成されるスケールがFeOだけでなく、Fe3O4やFe2O3といった生成物を混合して含有するスケールが形成される。 Even when a normal steel sheet containing Si or Cr is oxidized in the atmosphere, a mixed phase of FeO, FeCr 2 O 4 , and Fe 2 SiO 4 is formed at the interface with the substrate. However, since ordinary steel plates are easily oxidized, FeCr 2 O 4 and Fe 2 SiO 4 are formed unevenly, and the oxidation inhibiting effect is not fully exhibited, and therefore, the scale formed on the mixed phase However, not only FeO but also a mixture containing products such as Fe 3 O 4 and Fe 2 O 3 is formed.
つまり、大気酸化させた場合、基板との界面に生成したFeO、FeCr2O4、Fe2SiO4の混合相と、その上に生成した実質上FeOの単相とから成るスケールが形成される鋼板は、酸化が本質的にし難い。すなわち、本発明にかかる鋼板によれば、いかなる雰囲気において酸化させてもスケール生成量が少ない。 That is, when the atmosphere is oxidized, a scale composed of a mixed phase of FeO, FeCr 2 O 4 and Fe 2 SiO 4 generated at the interface with the substrate and a substantially single phase of FeO generated thereon is formed. Steel sheets are essentially difficult to oxidize. That is, according to the steel sheet according to the present invention, the amount of scale generation is small even when oxidized in any atmosphere.
従って、熱処理時に本発明鋼板を使用すれば、生成スケール量を少なくすることができ、また熱間プレス時に使用すれば熱間プレス時にスケールが剥離して金型が汚染されることは抑制される。 Therefore, if the steel sheet of the present invention is used at the time of heat treatment, the amount of generated scale can be reduced, and if used at the time of hot pressing, it is possible to suppress the scale from peeling off and contaminating the mold during hot pressing. .
次に、本発明の実施例について説明する。
表1に示した組成を有する鋼板(板厚:1.6mm)を供試材とした。これらの鋼板は、実験室にて溶製したスラブを、常法に準じて熱間圧延、酸洗、および一部冷間圧延を行って製造した鋼板である。これらの鋼板を、1.6t×100w×100L(mm)の寸法に切断し、下記の洗浄処理を行ってから、大気雰囲気の加熱炉内で900℃×4分加熱して、加熱炉より取り出し、その直後に平板の鋼製金型を用いて、熱間プレスを行った。
Next, examples of the present invention will be described.
A steel plate (thickness: 1.6 mm) having the composition shown in Table 1 was used as a test material. These steel plates are steel plates manufactured by subjecting a slab melted in a laboratory to hot rolling, pickling, and partial cold rolling according to a conventional method. These steel sheets were cut into dimensions of 1.6 t x 100 w x 100 L (mm), subjected to the following cleaning treatment, heated in an air atmosphere heating furnace at 900 ° C. for 4 minutes, and taken out from the heating furnace. Immediately thereafter, hot pressing was performed using a flat steel mold.
その後、X線回折装置や電子プローブマイクロアナライザーを用いて、生成スケール相の同定を行った。またFeO体積率評価については、断面ミクロ組織観察を行い、断面での面積率をもって体積率とし、その評価を行った。 Thereafter, the generated scale phase was identified using an X-ray diffractometer or an electron probe microanalyzer. For the FeO volume fraction evaluation, cross-sectional microstructure was observed, and the area ratio in the cross section was taken as the volume fraction, and the evaluation was performed.
上記洗浄処理は、以下のようにして行った。ナイロン製ブラシを用いて鋼板表面に数秒間水洗を行った。このときの水温度は50℃とした。次に日本表面化学製ジャスコピクル21A溶液(硫酸とリン酸の混合溶液−温度50℃)に数秒間浸漬した。次にオルソ珪酸ナトリウム水溶液(濃度2.9〜4.0%)を用いて、ナイロン製ブラシで鋼板表面を数秒間洗浄した。次にナイロン製ブラシを用いて鋼板表面に数秒間水洗を行った。このときの水温度は40℃とした。最後に防錆のため出光興産製SKW92を鋼板表面に塗布した。 The washing treatment was performed as follows. The steel plate surface was washed with water for several seconds using a nylon brush. The water temperature at this time was 50 ° C. Next, it was immersed for several seconds in a Juscopic 21A solution (mixed solution of sulfuric acid and phosphoric acid—temperature 50 ° C.) manufactured by Nippon Surface Chemicals. Next, using a sodium orthosilicate aqueous solution (concentration 2.9 to 4.0%), the steel plate surface was washed with a nylon brush for several seconds. Next, the steel plate surface was washed with water for several seconds using a nylon brush. The water temperature at this time was 40 ° C. Finally, SKW92 made by Idemitsu Kosan Co., Ltd. was applied to the steel plate surface for rust prevention.
本例における酸化抑制効果は、表層におけるスケールのFeO面積率で評価するものであり、熱間プレスに際しての均一スケールの生成能力の有無を云う。
本発明にかかる鋼板である鋼種No.1〜6では、FeO面積率がいずれも98%であり、酸化されがたい鋼板であることがわかる。
The oxidation suppression effect in this example is evaluated by the FeO area ratio of the scale in the surface layer, and indicates the presence or absence of the ability to generate a uniform scale during hot pressing.
In steel types Nos. 1 to 6, which are steel plates according to the present invention, the FeO area ratio is 98%, indicating that the steel plates are difficult to be oxidized.
一方、比較例である鋼種No.7では、洗浄処理が無く酸化が進行するため、FeO面積率が低くなっており、酸化抑制効果の無い鋼板であることがわかる。また鋼種No.8では、表面平均粗さが大きく酸化が進行するため、FeO面積率が低くなっており、酸化抑制効果の無い鋼板であることがわかる。また鋼種No.9では、Si及びCrが鋼中に含まれておらず酸化が進行するため、FeO面積率が低くなっており、酸化抑制効果の無い鋼板であることがわかる。 On the other hand, in steel type No. 7, which is a comparative example, since the oxidation proceeds without cleaning treatment, the FeO area ratio is low, indicating that the steel plate has no oxidation suppression effect. In Steel Type No. 8, since the surface average roughness is large and oxidation proceeds, the FeO area ratio is low, indicating that the steel plate has no oxidation inhibiting effect. Moreover, in steel type No. 9, since Si and Cr are not contained in the steel and oxidation proceeds, the FeO area ratio is low, and it can be seen that the steel plate has no oxidation inhibiting effect.
表1に示すのはいずれも冷間圧延材であるが、熱間圧延材に酸洗処理を行って得た鋼板についても同様の評価試験を行ったところ、実質上同一の結果を得た。 Although all shown in Table 1 are cold-rolled materials, a similar evaluation test was performed on steel sheets obtained by subjecting hot-rolled materials to pickling, and substantially the same results were obtained.
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