JP2011117086A - High-strength hardened body having excellent corrosion resistance and fatigue resistance - Google Patents
High-strength hardened body having excellent corrosion resistance and fatigue resistance Download PDFInfo
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- 238000005260 corrosion Methods 0.000 title claims abstract description 40
- 230000007797 corrosion Effects 0.000 title claims abstract description 39
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 32
- 239000010959 steel Substances 0.000 claims abstract description 32
- 229910052725 zinc Inorganic materials 0.000 claims abstract description 30
- 238000000034 method Methods 0.000 claims abstract description 18
- 229910052742 iron Inorganic materials 0.000 claims abstract description 14
- 229910001335 Galvanized steel Inorganic materials 0.000 claims abstract description 13
- 239000008397 galvanized steel Substances 0.000 claims abstract description 13
- 239000000203 mixture Substances 0.000 claims abstract description 8
- 238000005868 electrolysis reaction Methods 0.000 claims abstract description 7
- 239000007864 aqueous solution Substances 0.000 claims abstract description 5
- ZOMNIUBKTOKEHS-UHFFFAOYSA-L dimercury dichloride Chemical class Cl[Hg][Hg]Cl ZOMNIUBKTOKEHS-UHFFFAOYSA-L 0.000 claims abstract description 5
- 239000011701 zinc Substances 0.000 claims description 55
- 238000010438 heat treatment Methods 0.000 claims description 41
- 239000000463 material Substances 0.000 claims description 39
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims description 24
- 238000010791 quenching Methods 0.000 claims description 24
- 238000007747 plating Methods 0.000 claims description 23
- 230000000171 quenching effect Effects 0.000 claims description 23
- 238000005275 alloying Methods 0.000 claims description 8
- 239000008151 electrolyte solution Substances 0.000 claims description 5
- 230000001590 oxidative effect Effects 0.000 claims description 4
- 238000009740 moulding (composite fabrication) Methods 0.000 claims 1
- 239000003792 electrolyte Substances 0.000 abstract description 2
- 239000000243 solution Substances 0.000 abstract description 2
- 238000005244 galvannealing Methods 0.000 abstract 1
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 30
- 238000001816 cooling Methods 0.000 description 19
- 230000000052 comparative effect Effects 0.000 description 11
- 229910000640 Fe alloy Inorganic materials 0.000 description 6
- 238000005336 cracking Methods 0.000 description 6
- 238000012545 processing Methods 0.000 description 6
- 230000000694 effects Effects 0.000 description 5
- 229910001297 Zn alloy Inorganic materials 0.000 description 4
- 229910052782 aluminium Inorganic materials 0.000 description 4
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 4
- 239000007789 gas Substances 0.000 description 4
- 238000004519 manufacturing process Methods 0.000 description 4
- 229910052760 oxygen Inorganic materials 0.000 description 4
- 239000001301 oxygen Substances 0.000 description 4
- 230000000979 retarding effect Effects 0.000 description 4
- 238000009792 diffusion process Methods 0.000 description 3
- 238000005516 engineering process Methods 0.000 description 3
- 238000007731 hot pressing Methods 0.000 description 3
- 238000005482 strain hardening Methods 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 229910001566 austenite Inorganic materials 0.000 description 2
- 239000010953 base metal Substances 0.000 description 2
- 238000009835 boiling Methods 0.000 description 2
- 238000001704 evaporation Methods 0.000 description 2
- 230000008020 evaporation Effects 0.000 description 2
- 230000006698 induction Effects 0.000 description 2
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 2
- 229910000734 martensite Inorganic materials 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- PCTMTFRHKVHKIS-BMFZQQSSSA-N (1s,3r,4e,6e,8e,10e,12e,14e,16e,18s,19r,20r,21s,25r,27r,30r,31r,33s,35r,37s,38r)-3-[(2r,3s,4s,5s,6r)-4-amino-3,5-dihydroxy-6-methyloxan-2-yl]oxy-19,25,27,30,31,33,35,37-octahydroxy-18,20,21-trimethyl-23-oxo-22,39-dioxabicyclo[33.3.1]nonatriaconta-4,6,8,10 Chemical compound C1C=C2C[C@@H](OS(O)(=O)=O)CC[C@]2(C)[C@@H]2[C@@H]1[C@@H]1CC[C@H]([C@H](C)CCCC(C)C)[C@@]1(C)CC2.O[C@H]1[C@@H](N)[C@H](O)[C@@H](C)O[C@H]1O[C@H]1/C=C/C=C/C=C/C=C/C=C/C=C/C=C/[C@H](C)[C@@H](O)[C@@H](C)[C@H](C)OC(=O)C[C@H](O)C[C@H](O)CC[C@@H](O)[C@H](O)C[C@H](O)C[C@](O)(C[C@H](O)[C@H]2C(O)=O)O[C@H]2C1 PCTMTFRHKVHKIS-BMFZQQSSSA-N 0.000 description 1
- 229910018072 Al 2 O 3 Inorganic materials 0.000 description 1
- 229910000760 Hardened steel Inorganic materials 0.000 description 1
- 229910004298 SiO 2 Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 230000004888 barrier function Effects 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 238000005261 decarburization Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 230000008034 disappearance Effects 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 238000005246 galvanizing Methods 0.000 description 1
- KFZAUHNPPZCSCR-UHFFFAOYSA-N iron zinc Chemical compound [Fe].[Zn] KFZAUHNPPZCSCR-UHFFFAOYSA-N 0.000 description 1
- 238000005461 lubrication Methods 0.000 description 1
- 238000000691 measurement method Methods 0.000 description 1
- 230000007935 neutral effect Effects 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 230000035515 penetration Effects 0.000 description 1
- 230000002265 prevention Effects 0.000 description 1
- 230000001681 protective effect Effects 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000004904 shortening Methods 0.000 description 1
- 238000010583 slow cooling Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
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- Coating With Molten Metal (AREA)
- Heat Treatments In General, Especially Conveying And Cooling (AREA)
Abstract
Description
本発明は、耐食性、耐疲労性に優れ高強度化を目的とした焼き入れ加工を施してなる成形体に関するものである。 The present invention relates to a molded article that is excellent in corrosion resistance and fatigue resistance and is subjected to quenching for the purpose of increasing strength.
近年、自動車の軽量化、安全性向上を目的として自動車部品およびそれに使用される素材の高強度化が進められており、その代表的な素材である鋼板も高強度鋼板の使用比率が高まってきている。しかしながら、高強度鋼板は一般に、高強度で硬いが故に、プレス成形性での、成形自由度が小さく、またプレス製品の形状凍結性が悪く成形品の寸法精度が不良、プレス金型の寿命が短いなどの課題がある。これらの課題に対して素材からの改善も進められているが、近年より一層の高強度部品を形状精度良く得ることを目的に、鋼板を８００℃以上に加熱して柔らかくし、プレス成形と同時に急速に冷却し、焼き入れして高強度の部品とする、熱間加工、ホットプレス技術が普及してきており、また冷間で加工後同様に焼入れして高強度の部品とする冷間加工−焼き入れ技術も工業技術として使用されるようになってきた。 In recent years, the strength of automobile parts and materials used for them has been increased for the purpose of reducing the weight and safety of automobiles, and the use ratio of high-strength steel sheets is increasing for steel plates that are representative materials. Yes. However, high-strength steel sheets are generally high-strength and hard, so the press formability is low, the degree of freedom of forming is low, the shape freezeability of the pressed product is poor, the dimensional accuracy of the molded product is poor, and the press mold life is shortened. There are issues such as shortness. Although improvements from the raw materials have been promoted for these problems, the steel plate is heated to 800 ° C. or more to be softened in order to obtain higher strength parts with higher shape accuracy in recent years. Hot working and hot pressing technology that rapidly cools and quenches to make high strength parts have become widespread, and cold working to make high strength parts after quenching in the same way- Quenching technology has also been used as an industrial technology.
一方、自動車に代表される産業機械は、使用環境における耐食性が十分必要な為、現在、低コストで耐食性に優れる亜鉛系めっき鋼板を冷間で成形した部品が使用されており、表面処理鋼材を加熱焼入れする多くの発明が公知である。 On the other hand, because industrial machinery represented by automobiles requires sufficient corrosion resistance in the usage environment, parts that are cold-formed zinc-coated steel sheets that are low in cost and excellent in corrosion resistance are currently used. Many inventions for heat quenching are known.
例えば特許文献１には、加熱、冷却により亜鉛または亜鉛合金を５μｍ〜３０μｍにより腐食、脱炭の保護と潤滑機能を確保した高強度の成形部品の製造方法が、特許文献２には加熱時の亜鉛の蒸発を防止するバリア層を備えた熱間プレス用鋼板が、特許文献３には亜鉛系めっき鋼板の熱間プレス方法が、特許文献４には鉄−亜鉛固溶層が存在する熱間プレス成形品が開示されている。しかしながら、これらの方法は、何れもめっきの無い鉄を焼入れした成型品よりは耐食性に優れるものの、通常の冷間加工にて成型されためっき鋼板の成型品の耐食性と比べると不十分である。これら問題に対し、通常のめっき鋼板並みに耐食性が要求される用途には、アルミめっき鋼板が使用されているが、コストが高いだけでなく、やはり焼入れ後の耐食性は冷間成型材より低下する。一方、これら亜鉛系めっき材は粒界にわれを生じやすく、割れを回避するために、事前に冷間で加工した後に焼き入れるための方法があるが、生産性が悪いなどの問題がある。これら問題に対し溶接性、コストでより優位な亜鉛系めっき材で生産性良く、焼き入れ高強度鋼材を生産する技術が強く望まれている。
For example,
本発明は上記の問題に鑑み、コスト的に優位な亜鉛系めっき鋼材にて、生産性に優れた方法で、焼き入れ後の成形品の耐食性を冷間成型品と同等以上とした、耐食性と粒界割れを回避して耐疲労性に優れた高強度焼き入れ成形体を提供することを目的とするものである。 In view of the above problems, the present invention is a cost-effective zinc-based plated steel material, and is a method with excellent productivity, and the corrosion resistance of a molded product after quenching is equal to or higher than that of a cold molded product, An object of the present invention is to provide a high-strength quenched molded body that is excellent in fatigue resistance by avoiding intergranular cracking.
本発明者は、まず焼き入れるのに必要な８００℃以上の熱間加工後で、亜鉛系めっき鋼材の耐食性が通常の亜鉛めっき鋼材、例えば合金化溶融亜鉛めっき鋼板の耐食性より劣る原因について鋭意検討を行った。この結果、耐食性が劣化する原因はＺｎが揮発しめっき量が減じる為のみならず、めっき層がＦｅ中に固溶してＦｅを主体としたＦｅ−Ｚｎ合金層となる為であるとの結論に達した。つまり、通常の亜鉛めっき鋼材は、犠牲防食効果以上に、腐食時に酸化されるＺｎが緻密な保護膜となる効果により耐食性が発揮される。しかしながら、８００℃以上の熱間加工された亜鉛系めっき鋼材は、Ｆｅ−Ｚｎ合金層が、通常の亜鉛系めっき鋼材よりもＺｎ分として鋼材表面に量的に十二分にあっても耐食性は発揮されない。これは、通常焼き入れによって生成したＦｅ−Ｚｎ合金層はＦｅが主体となっている為、腐食時に酸化されたＦｅの体積膨張により、Ｚｎの酸化膜が緻密となりえないためである。故に、耐食性を発揮させるには、Ｚｎを主体とした質の良いＺｎ−Ｆｅ合金層が量的にも十分にあることが重要である。また、焼き入れ強度と耐食性とを両立させるためには、加熱温度や急冷速度などの条件が重要であり、ホットスタンプ時の加工による母材の粒界割れを抑制するために、ホットスタンプ工程に入る直前において所定条件で急冷する必要があることが判明した。 The present inventor first studied earnestly about the cause that the corrosion resistance of the galvanized steel material is inferior to that of a normal galvanized steel material, for example, an alloyed hot-dip galvanized steel sheet, after hot working at 800 ° C. or higher necessary for quenching. Went. As a result, it is concluded that the corrosion resistance is deteriorated not only because Zn volatilizes and the amount of plating decreases, but also because the plating layer becomes a Fe—Zn alloy layer mainly composed of Fe by solid solution in Fe. Reached. That is, the normal galvanized steel material exhibits corrosion resistance more than the sacrificial anticorrosive effect due to the effect that Zn oxidized during corrosion becomes a dense protective film. However, the hot-worked zinc-based plated steel material of 800 ° C. or higher has corrosion resistance even if the Fe—Zn alloy layer is more than the amount of Zn on the steel material surface as the Zn content than normal zinc-based plated steel material. It is not demonstrated. This is because the Fe—Zn alloy layer generated by normal quenching is mainly composed of Fe, so that the Zn oxide film cannot become dense due to the volume expansion of Fe oxidized during corrosion. Therefore, in order to exhibit the corrosion resistance, it is important that the Zn-Fe alloy layer of good quality mainly composed of Zn is sufficient in quantity. Also, in order to achieve both quenching strength and corrosion resistance, conditions such as heating temperature and quenching speed are important, and in order to suppress intergranular cracking of the base metal due to processing during hot stamping, It turned out that it was necessary to cool rapidly under predetermined conditions immediately before entering.
本発明は上記の知見に基づいてなされたものであって、本発明の耐食性、耐疲労性に優れた高強度焼き入れ成形体は、亜鉛めっき系鋼材をホットスタンプのため加熱し、成形して焼き入れした高強度焼き入れ成形体であって、焼き入れ後の成形体鋼材表面に、Ｚｎを主成分とし、合金化遅延機能および易酸化性機能を有するＡｌを単独で０．１５質量％以上含有し、Ｆｅが下記測定方法で９質量％以上、３０質量％以下である亜鉛めっき層が、３０ｇ／ｍ２以上形成されていることを特徴とするものである。なお本発明における亜鉛めっき層中のＦｅ濃度測定方法は、「ＮＨ４Ｃｌ：１５０ｇ／ｌの水溶液中で４ｍＡ／ｃｍ２で飽和カロメル電極を参照電極として定電流電解により−８００ｍＶｖｓ．ＳＣＥ以下に大きく変化する点でのГ層までを電解し電解液をＩＣＰによりＦｅ、Ｚｎの量、組成比を測定する方法」である。 The present invention has been made on the basis of the above knowledge, and the high-strength quenched molded body having excellent corrosion resistance and fatigue resistance according to the present invention is formed by heating and forming a galvanized steel material for hot stamping. Quenched high-strength quenched molded body, on the surface of the molded steel material after quenching, Zn is the main component, and Al having an alloying delay function and an easily oxidizable function alone is 0.15% by mass or more A galvanized layer containing Fe in an amount of 9% by mass to 30% by mass in the following measurement method is formed in an amount of 30 g / m 2 or more. The method for measuring the Fe concentration in the galvanized layer in the present invention is as follows: “NH 4 Cl: in an aqueous solution of 150 g / l, 4 mA / cm 2 and a saturated calomel electrode as a reference electrode, and a large current of −800 mV vs. “Method of electrolyzing up to Γ layer at changing point and measuring amount and composition ratio of Fe and Zn by ICP of electrolyte”.
本発明によれば、亜鉛めっき層のＺｎの地鉄への拡散を飛躍的に抑制して質のよいZn-Fe合金層を量的にも十分確保でき、かつ、めっき表面で緻密な酸化皮膜を形成しめっき量を確保するため、コスト的に優位な亜鉛めっき鋼材を用いて、冷間成型品と同等以上の耐食性を発揮する高強度焼き入れ成形体を製造することが可能となる。また温度条件、急冷条件を特定したことにより、焼き入れ性が良好でしかも加工時の母材に粒界割れのない高強度焼き入れ成形体を得ることができる。 According to the present invention, a Zn-Fe alloy layer having a high quality can be sufficiently secured in a quantitative manner by dramatically suppressing the diffusion of Zn in the galvanized layer to the ground iron, and a dense oxide film on the plating surface. Therefore, it is possible to manufacture a high-strength quenched molded body that exhibits corrosion resistance equivalent to or better than that of a cold-molded product using a galvanized steel material that is superior in cost. Further, by specifying the temperature condition and the rapid cooling condition, it is possible to obtain a high-strength quenched molded body having good quenchability and free from grain boundary cracks in the base material during processing.
以下、本発明について詳細に説明する。
まず、本発明の耐食性に優れた高強度焼き入れ成形体は、合金化遅延機能および易酸化機能を有するＡｌ，Ｓｉを各々単独もしくは複合して０．１５質量％以上含有する亜鉛めっき層を備えた亜鉛めっき鋼材を母材とし、これを酸素０．１体積％以上の酸化雰囲気下で８００℃以上９５０℃以下に加熱後、７３０℃以下５００℃以上に６０sec以内で冷却した後、加工急冷することで得られる。鋼材としては、通常の焼き入れ鋼材なら何れでも使用可能であるが、質量％にて、Ｃ：０．１５％以上、Ｍｎ：０．５％以上、Ｃｒ：０．１％以上、Ｂ：０．０００５％以上を含有するものであることが好ましい。
Hereinafter, the present invention will be described in detail.
First, the high-strength quench-molded article excellent in corrosion resistance according to the present invention includes a galvanized layer containing 0.15% by mass or more of Al and Si each having an alloying delay function and an easily oxidizable function, either alone or in combination. A galvanized steel material is used as a base material, heated to 800 ° C. or higher and 950 ° C. or lower in an oxidizing atmosphere containing 0.1% by volume or more of oxygen, cooled to 730 ° C. or lower and 500 ° C. or higher within 60 seconds, and then rapidly quenched. Can be obtained. As a steel material, any ordinary hardened steel material can be used, but in mass%, C: 0.15% or more, Mn: 0.5% or more, Cr: 0.1% or more, B: 0 It is preferable that it contains 0.005% or more.
Ｚｎのめっき量としては目的とする耐食目標にもよるが、４０ｇ／ｍ２以上あれば良いが、加熱炉のハンドリングの時間、温度の変動を考慮し、好ましくは６０ｇ／ｍ２以上、炉内での鋼材の置き方による亜鉛の垂れを考慮すれば３００ｇ／ｍ２以下が好ましく、特に垂直に置いても垂れの発生が殆ど認められない１８０ｇ／ｍ２以下が好ましい。亜鉛系めっき鋼材は、溶融亜鉛めっき法で作成されたものが良く、事前に合金化された合金化溶融亜鉛めっき材は合金化遅延元素の余分な消失を招き効果が低減し、電気亜鉛めっき法では合金化遅延元素の添加にプレ処理がいるなどコストがかかるので好ましくない。 Although the amount of Zn plating depends on the target corrosion resistance target, it should be 40 g / m 2 or more, but considering the handling time and temperature fluctuation of the heating furnace, preferably 60 g / m 2 or more, In consideration of the sag of zinc due to the way the steel material is placed, the amount is preferably 300 g / m 2 or less, and particularly preferably 180 g / m 2 or less where the occurrence of sag is hardly observed even when placed vertically. Zinc-based galvanized steel materials are preferably prepared by hot dip galvanizing, and pre-alloyed galvanized steel materials cause excessive disappearance of alloying delay elements, reducing the effect, and electrogalvanizing In this case, it is not preferable because the pretreatment is required to add the alloying retarding element.
通常、８００℃以上の熱間加工ではＺｎは十分な蒸気圧を有する為、加熱炉内に揮散する。易酸化性元素としてＡｌ、ＳｉをＺｎめっき層中に０．１５質量％以上含有させ、かつ炉内を０．１体積％以上酸素の存在する酸化雰囲気下としてやることで、めっき表面で易酸化性元素が、熱による膨張変化に対しても継続的に酸化され緻密な酸化皮膜を形成する為、８００℃以上９５０℃以下の加熱温度範囲でＺｎの蒸発の抑制が可能となる。逆に、これら易酸化性元素が０．１５質量％未満あるいは炉内雰囲気が酸素０．１体積％未満の中性〜還元雰囲気下では亜鉛表面に易酸化性元素の緻密な皮膜を十分形成できずＺｎの揮散がなされ防錆のためのＺｎ量が減じられる。また、加熱温度が８００℃未満では、Ｚｎの揮発防止には有利であるが、本来の目的である高強度成形体を得る為の焼き入れがなされず、９５０℃超では易酸化性元素による酸化膜をもってしてもＺｎの沸騰による揮散を抑えることが出来ない。以上の手段により加熱によるＺｎの揮発は大きく抑制できる。 Usually, in hot working at 800 ° C. or higher, Zn has a sufficient vapor pressure, and therefore volatilizes in the heating furnace. Easily oxidize on the plating surface by containing 0.15% by mass or more of Al or Si as an easily oxidizable element in the Zn plating layer and making the inside of the furnace in an oxidizing atmosphere containing 0.1% by volume or more of oxygen. Since the oxidative element is continuously oxidized against the expansion change due to heat to form a dense oxide film, the evaporation of Zn can be suppressed in the heating temperature range of 800 ° C. or higher and 950 ° C. or lower. Conversely, a dense film of easily oxidizable elements can be sufficiently formed on the zinc surface in a neutral to reducing atmosphere where these oxidizable elements are less than 0.15 mass% or the furnace atmosphere is less than 0.1 volume% oxygen. Zinc is volatilized and the amount of Zn for rust prevention is reduced. Further, if the heating temperature is less than 800 ° C., it is advantageous for preventing the volatilization of Zn. However, if the heating temperature is higher than 950 ° C., oxidation by an easily oxidizable element is not performed. Even with a film, volatilization due to boiling of Zn cannot be suppressed. By the above means, volatilization of Zn by heating can be greatly suppressed.
さらに、耐食性を通常のめっき同等以上にするには、Ｚｎを主体としたＦｅ：３０質量％以下からなるＺｎ−Ｆｅ合金層を３０ｇ／ｍ２以上にしなければならない。３０ｇ／ｍ２未満では、焼き入れ時の加熱により生成されるめっき層がＦｅを主体とした合金層となり腐食時にＦｅ錆を生じ体積膨張するので十分な耐食性が得られない。さらに、合金化遅延元素として易酸化性元素を兼ねるＡｌ，Ｓｉを各々単独もしくは複合して０．１５質量％以上含有することが重要である。これらの元素が、加熱前の亜鉛めっき層中に０．１５質量％以上あれば、８００℃以上の高温の加熱でも飛躍的にＺｎの地鉄への拡散を抑制できるので、Ｆｅ：３０質量％以下からなるＺｎ−Ｆｅ合金層を３０ｇ／ｍ２以上にすることができる。逆に、０．１５質量％未満では合金化遅延効果が失われるためＺｎの地鉄への拡散が速すぎて、鋼材の温度が８００℃に到達するまでにＺｎを主体としたＦｅ：３０質量％以下からなるＺｎ−Ｆｅ合金層が、殆ど消失し耐食性が発揮されない。なお、亜鉛めっき層中のＦｅ濃度測定方法は、ＮＨ４Ｃｌ：１５０ｇ／ｌの水溶液中で４ｍＡ／ｃｍ２で飽和カロメル電極を参照電極として定電流電解により−８００ｍＶｖｓ．ＳＣＥ以下に大きく変化する点でのГ層までを電解し電解液をＩＣＰによりＦｅ、Ｚｎの量、組成比を測定する方法である。 Furthermore, in order to make the corrosion resistance equal to or higher than that of normal plating, the Zn—Fe alloy layer composed mainly of Zn: Fe: 30% by mass or less must be 30 g / m 2 or more. If it is less than 30 g / m 2 , the plated layer produced by heating during quenching becomes an alloy layer mainly composed of Fe, and Fe rust is generated during corrosion and volume expansion occurs, so that sufficient corrosion resistance cannot be obtained. Furthermore, it is important to contain 0.15% by mass or more of Al and Si, which also serve as easily oxidizable elements, as alloying retarding elements, each alone or in combination. If these elements are 0.15% by mass or more in the galvanized layer before heating, the diffusion of Zn into the ground iron can be remarkably suppressed even by heating at a high temperature of 800 ° C. or higher, so that Fe: 30% by mass The Zn—Fe alloy layer comprising the following can be made 30 g / m 2 or more. On the contrary, if the content is less than 0.15% by mass, the effect of retarding alloying is lost, so that diffusion of Zn into the ground iron is too fast, and Fe: 30 masses mainly composed of Zn until the temperature of the steel material reaches 800 ° C. % Of Zn—Fe alloy layer is almost disappeared and corrosion resistance is not exhibited. The method for measuring the Fe concentration in the galvanized layer was -800 mV vs. by constant current electrolysis using a saturated calomel electrode as a reference electrode at 4 mA / cm 2 in an aqueous solution of NH 4 Cl: 150 g / l. In this method, electrolysis is performed up to the Γ layer at a point that greatly changes to SCE or less, and the amount and composition ratio of Fe and Zn are measured by ICP of the electrolytic solution.
本発明では上記のような亜鉛めっき鋼材を、８００℃以上９５０℃以下に加熱する。加熱時間は、加熱する鋼材（鋼板）の厚み（板厚）によるが、Ｚｎ７０％以上のめっき層を３０ｇ／ｍ２以上残すようにする。鋼材全体が焼き入れに必要な温度に到達すればよい。また、加熱時間が、鋼材の厚みや炉長、ハンドリング装置により長くなる場合は、単位面積あたりのめっき層中の合金化遅延元素量を増加（めっき層中のこれら元素の濃度増やめっき量の増）させることが好ましい。加熱方法は、誘導加熱のような内部加熱でも、赤外加熱、ガス加熱、電気炉のような外部加熱でも、加熱時間短縮の為これらの併用の何れでも良い。 In the present invention, the above galvanized steel is heated to 800 ° C. or higher and 950 ° C. or lower. The heating time depends on the thickness (plate thickness) of the steel material (steel plate) to be heated, but a plating layer of Zn 70% or more is left at 30 g / m 2 or more. It is only necessary that the entire steel material reaches a temperature necessary for quenching. Also, when the heating time becomes longer due to the thickness of steel, furnace length, or handling equipment, increase the amount of alloying retarding elements in the plating layer per unit area (increasing the concentration of these elements in the plating layer or the amount of plating) Increase). The heating method may be internal heating such as induction heating, infrared heating, gas heating, external heating such as an electric furnace, or any combination thereof for shortening the heating time.
加熱温度は前記したように８００℃以上９５０℃以下とする。８００℃未満では焼き入れに必要な母材のＡｃ３点を超えないので焼き入れ不足となり、十分な強度が得られない。また９５０℃を超えると亜鉛めっき層中の亜鉛が沸騰揮散するので好ましくない。８００℃以上９５０℃以下の温度域では亜鉛の沸騰をＡｌ２Ｏ３、ＳｉＯ２の酸化膜で防止することができる。 As described above, the heating temperature is set to 800 ° C. or more and 950 ° C. or less. If it is less than 800 ° C., it does not exceed the Ac 3 point of the base material necessary for quenching, so that quenching is insufficient and sufficient strength cannot be obtained. On the other hand, when the temperature exceeds 950 ° C., the zinc in the galvanized layer evaporates and is not preferable. In the temperature range of 800 ° C. or higher and 950 ° C. or lower, boiling of zinc can be prevented by an oxide film of Al 2 O 3 or SiO 2 .
本発明では、亜鉛めっき層を十分固化してホットスタンプ加工時における母材の粒界割れを抑制するために、加熱設備である炉から取り出した後に、７３０℃以下５００℃以上に６０sec以内で冷却する。この亀裂は母材の引っ張り側において発生するもので、本発明者の検討によれば母材の旧オーステナイト粒界に溶融亜鉛が浸入することが原因である。そこで図１に示すように、加熱設備１とホットスタンプ設備３との間に、加熱された亜鉛めっき鋼板を急冷する設備２を設け、７３０℃以下にまで６０sec以内で急冷する。７３０℃以下に冷却すれば溶融亜鉛の浸入はなくなり、ホットスタンプ加工時における母材表面の亀裂を防止できる。なおこのための冷却手段としては、ガス冷却または気水冷却が適当である。また、冷却設備は加熱設備とホットスタンプ設備の間にあればよく、その態様としてゾーンでもよく、また加熱設備からホットスタンプ設備へ移送する設備に付加し移送しながら冷却する方法でも良い。
In the present invention, in order to sufficiently solidify the galvanized layer and suppress intergranular cracking of the base material during hot stamping, it is cooled to 730 ° C. or lower and 500 ° C. or higher within 60 seconds after being taken out from the furnace. To do. This crack is generated on the tensile side of the base material, and according to the study of the present inventor, it is caused by the penetration of molten zinc into the prior austenite grain boundary of the base material. Therefore, as shown in FIG. 1, a
このように本発明ではホットスタンプ加工の開始前に亜鉛を固化させるための冷却が行われるが、ホットスタンプ加工はオーステナイト状態で行われることが好ましく、このためホットスタンプ加工前の母材温度は５００℃以上とする。５００℃未満ではマルテンサイトが生成されてしまい、成形性が悪化するからである。また冷却時間は６０秒以内とする。冷却をこれよりゆっくりと行うとフェライトが生成されて軟質となり、目的とする高強度が得られないからである。 As described above, in the present invention, cooling for solidifying zinc is performed before the start of hot stamping, but the hot stamping is preferably performed in an austenite state. Therefore, the base material temperature before hot stamping is 500. ℃ or more. This is because if it is less than 500 ° C., martensite is generated and the moldability deteriorates. The cooling time is 60 seconds or less. This is because if cooling is performed more slowly than this, ferrite is generated and becomes soft, and the desired high strength cannot be obtained.
その後に加工急冷を伴うホットスタンプ設備においてホットスタンプ加工が行われ、所望形状に加工される。形状確保と焼き入れのために、母材を３０℃/sec以上で２００℃以下まで加工急冷することが好ましい。これによりＺｎ７０%以上のめっき層を３０ｇ／ｍ２以上持つ高強度高耐食成形体を製造することができる。 Thereafter, hot stamping is performed in a hot stamping facility that involves rapid cooling of the workpiece, and the workpiece is processed into a desired shape. For securing the shape and quenching, it is preferable to rapidly quench the base material at 30 ° C./sec or more to 200 ° C. or less. As a result, a high-strength, high-corrosion-resistant molded body having a Zn 70% or more plating layer of 30 g / m 2 or more can be produced.
以下に本発明の実施例を示す。
表１に示すＡＢＣＤの鋼材を用い、表２に示す条件で亜鉛めっきと加熱とを行った。めっき処理条件（めっき方法、めっき量、内Ｚｎ量、組成、上層めっき）とめっき処理の施された鋼板に対して加熱する加熱条件（加熱方法、加熱温度、保持時間、加熱雰囲気、酸素濃度）とを表２に示す。更に、加熱後の鋼板に対して表３に示す条件で冷却とホットスタンプによる加工焼き入れとを行った。熱間処理は大気雰囲気下または所定空気比の雰囲気下にて電気炉または高周波誘導加熱炉またはガス炉または赤外加熱炉を用い、鋼板を加熱し、炉から鋼板を取り出し、その後、該鋼板を水冷または金型冷却またはガス冷却した。
Examples of the present invention are shown below.
Using the ABCD steel materials shown in Table 1, galvanization and heating were performed under the conditions shown in Table 2. Plating treatment conditions (plating method, plating amount, inner Zn amount, composition, upper layer plating) and heating conditions for heating the steel plate subjected to plating treatment (heating method, heating temperature, holding time, heating atmosphere, oxygen concentration) Are shown in Table 2. Furthermore, the steel plate after heating was subjected to cooling and work quenching by hot stamping under the conditions shown in Table 3. In the hot treatment, an electric furnace, a high frequency induction heating furnace, a gas furnace or an infrared heating furnace is used in an air atmosphere or an atmosphere having a predetermined air ratio, the steel plate is heated, and the steel plate is taken out from the furnace. Water cooled or mold cooled or gas cooled.
Ｚｎを主成分としてＦｅ：３０質量％以下からなる層は、めっき処理の施された鋼板に対し表２及び表３に示した各処理条件（加熱条件及び冷却方法）にて処理を施すことにより作成され、この層の作成によって得られた製造物を、ＮＨ４Ｃｌ：１５０ｇ／ｌの水溶液中で４ｍＡ／ｃｍ２で飽和カロメル電極を参照電極として定電流電解により−８００ｍＶ ｖｓ．ＳＣＥ以下に大きく変化する点のΓ層までを電解し電解液をＩＣＰにより測定し、防錆効果のあるめっき量としてＦｅ、Ｚｎの量、組成比を求め、それらを表３に示した。尚、Ｆｅ：３０％超のＺｎ−Ｆｅ合金層の測定は上記Γ層までの電解後、電解液を新しい液に代えて引き続き鉄の電位（約−５６０ｍＶ ｖｓ．ＳＣＥ）までを電解し、同様に電解液をＩＣＰにより測定しＦｅ、Ｚｎの量、組成比を求め、それらを表３に示した。
強度は、表３に示す条件で、金型を定盤にして冷却した後、ＪＩＳ５号引張試験片のＬ方向引張にて評価し、その評価結果を表３に示し、８００ＭＰａを超えるものを良好とした。
A layer composed of Zn as a main component and Fe: 30% by mass or less is obtained by subjecting a steel sheet subjected to plating treatment to the treatment conditions (heating conditions and cooling methods) shown in Tables 2 and 3. The product produced by the creation of this layer was subjected to constant current electrolysis at 4 mA / cm 2 in an aqueous solution of NH 4 Cl: 150 g / l using a saturated calomel electrode as a reference electrode at −800 mV vs. Electrolysis was performed up to the Γ layer at a point that greatly changed below SCE, and the electrolytic solution was measured by ICP. The amounts of Fe and Zn and the composition ratio were determined as plating amounts having a rust-preventing effect. In addition, the measurement of the Zn-Fe alloy layer of Fe: more than 30% was conducted by electrolyzing up to the Γ layer, and then electrolyzing up to the electric potential of iron (about -560 mV vs. SCE) by replacing the electrolytic solution with a new solution. The electrolyte solution was measured by ICP to determine the amounts and composition ratios of Fe and Zn, and these are shown in Table 3.
The strength was evaluated by L-direction tension of a JIS No. 5 tensile test piece after cooling the mold with a surface plate under the conditions shown in Table 3, and the evaluation results are shown in Table 3, and those exceeding 800 MPa are good. It was.
割れの有無は、表３に示す条件で、ホットスタンプつまりプレス加工・冷却して図２に示すような断面形状の試験片を作成し、曲げ部の断面観察を行い、割れの有無を調べた。その結果を表３に示す。
耐食性は、製造後の表面に対し、脱脂、およびパルボンドＬＡ３５（日本パーカーライジング社製）にて、メーカー処方通り化成処理を行い、さらにカチオン電着塗装（パワーニクス１１０：日本ペイント社製）を１５μｍ実施し、クロスカットを施した後、アメリカ自動車工業会規格ＳＡＥ−Ｊ２３３４腐食試験条件にて３００サイクル実施後のクロスカット部からの塗膜フクレ巾（片側）を測定した。その測定結果を表３に示す。
The presence / absence of cracks was determined by checking the presence / absence of cracks by creating a test piece having a cross-sectional shape as shown in FIG. . The results are shown in Table 3.
For corrosion resistance, the surface after production is degreased and subjected to chemical conversion treatment with Palbond LA35 (Nihon Parker Rising Co., Ltd.) as prescribed by the manufacturer. After carrying out and carrying out the crosscut, the coating film width (one side) from the crosscut part after 300 cycles implementation on American Automobile Manufacturers Association standard SAE-J2334 corrosion test conditions was measured. The measurement results are shown in Table 3.
比較例１１はホットスタンプ加工前の急冷を行わなかった例で、加工時に母材の粒界割れが生じた。比較例１２は冷却に６０秒以上かけたため、焼きが入らず強度が低下している。比較例１３は５００℃以下にまで冷却したためマルテンサイトが生成され、加工中に破断した。比較例１４は加工中の冷却速度が遅いため強度が低下している。 Comparative Example 11 was an example in which rapid cooling before hot stamping was not performed, and grain boundary cracking of the base material occurred during processing. Since the comparative example 12 took 60 seconds or more for cooling, baking did not enter and the intensity | strength fell. Since the comparative example 13 was cooled to 500 degrees C or less, the martensite was produced | generated and it fractured | ruptured during processing. Since the comparative example 14 has a slow cooling rate during processing, the strength is low.
比較例１と比較例２は亜鉛めっき組成が本発明範囲を外れており、亜鉛揮発量が多く、耐食性が低下している。比較例３はめっき量が不足しており、耐食性が低下している。比較例４は加熱温度が低く、強度が出ない。比較例５は加熱過多のため、耐食性が低下している。比較例６は加熱温度が高すぎるため、亜鉛揮発量が多く耐食性が低下している。比較例７は還元雰囲気中で加熱したため、亜鉛揮発量が多く耐食性が低下している。 In Comparative Examples 1 and 2, the zinc plating composition is out of the scope of the present invention, the zinc volatilization amount is large, and the corrosion resistance is lowered. In Comparative Example 3, the plating amount is insufficient, and the corrosion resistance is reduced. In Comparative Example 4, the heating temperature is low and the strength does not appear. In Comparative Example 5, the corrosion resistance is lowered due to excessive heating. In Comparative Example 6, since the heating temperature is too high, the amount of volatilized zinc is large and the corrosion resistance is low. Since Comparative Example 7 was heated in a reducing atmosphere, the amount of volatilized zinc was large and the corrosion resistance was reduced.
このように本発明の範囲を外れた比較例では強度や耐食性が劣るが、本発明の範囲内にある実施例１１〜２６では、Ｚｎを主成分としてＦｅ：３０質量％以下からなる層が３０ｇ／ｍ２以上あり、また焼き入れの加熱により生成したＦｅを主体とする合金層が５ｇ／ｍ２以上形成されている。この結果、コスト的に優位な亜鉛系めっき鋼材にて、焼き入れ後の成形品の耐食性を冷間成型品と同等以上とした、耐食性と耐疲労性に優れた高強度焼き入れ成形体を得ることができる。 Thus, although the strength and corrosion resistance are inferior in the comparative example out of the scope of the present invention, in Examples 11 to 26 within the scope of the present invention, the layer composed of Zn as a main component and Fe: 30% by mass or less is 30 g. / m are 2 or more, are formed alloy layer consisting mainly of Fe produced by heating the quenching is 5 g / m 2 or more. As a result, a high-strength quenched molded body with excellent corrosion resistance and fatigue resistance is obtained, with the corrosion resistance of the molded product after quenching equal to or higher than that of cold molded products, with a zinc-based plated steel material that is superior in cost. be able to.
１ 加熱設備
２ 急冷設備
３ ホットスタンプ設備
1
Claims (1)
亜鉛めっき層中のＦｅ濃度測定方法；ＮＨ４Ｃｌ：１５０ｇ／ｌの水溶液中で４ｍＡ／ｃｍ２で飽和カロメル電極を参照電極として定電流電解により−８００ｍＶｖｓ．ＳＣＥ以下に大きく変化する点でのГ層までを電解し電解液をＩＣＰによりＦｅ、Ｚｎの量、組成比を測定する方法。 A high-strength quench-molded body obtained by heating, forming, and quenching a galvanized steel material for hot stamping. The surface of the molded steel material after quenching is mainly composed of Zn and has an alloying delay function and easy A zinc plating layer containing 0.15% by mass or more of Al having an oxidizing function and Fe of 9% by mass or more and 30% by mass or less by the following measuring method is formed in an amount of 30g / m 2 or more. A high-strength quenched and molded product with excellent corrosion resistance and fatigue resistance.
Method for measuring Fe concentration in galvanized layer; NH 4 Cl: −800 mV vs. by constant current electrolysis using saturated calomel electrode as reference electrode at 4 mA / cm 2 in an aqueous solution of 150 g / l. A method of electrolyzing up to the Γ layer at a point that greatly changes below SCE and measuring the amount and composition ratio of Fe and Zn by ICP of the electrolytic solution.
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| JP2013202619A (en) * | 2012-03-27 | 2013-10-07 | Aisin Takaoka Ltd | Hot press molding apparatus and hot press molding method |
| JP2014521833A (en) * | 2011-07-25 | 2014-08-28 | マグナ インターナショナル インコーポレイテッド | Products and processes by local heat treatment of sheet steel. |
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| CN109323062A (en) * | 2018-10-31 | 2019-02-12 | 武汉市计量测试检定（研究）所 | A kind of reducing type flow cardan and preparation method thereof |
| WO2021182465A1 (en) | 2020-03-12 | 2021-09-16 | 日本製鉄株式会社 | Plated steel plate for hot stamping |
| WO2024122124A1 (en) * | 2022-12-09 | 2024-06-13 | 日本製鉄株式会社 | Hot-stamp molded body |
| WO2024122118A1 (en) * | 2022-12-09 | 2024-06-13 | 日本製鉄株式会社 | Plated steel sheet |
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| WO2021182465A1 (en) | 2020-03-12 | 2021-09-16 | 日本製鉄株式会社 | Plated steel plate for hot stamping |
| KR20220154177A (en) | 2020-03-12 | 2022-11-21 | 닛폰세이테츠 가부시키가이샤 | Galvanized steel sheet for hot stamping |
| US11866828B2 (en) | 2020-03-12 | 2024-01-09 | Nippon Steel Corporation | Plated steel sheet for hot stamping |
| WO2024122124A1 (en) * | 2022-12-09 | 2024-06-13 | 日本製鉄株式会社 | Hot-stamp molded body |
| WO2024122118A1 (en) * | 2022-12-09 | 2024-06-13 | 日本製鉄株式会社 | Plated steel sheet |
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