JP5879390B2 - 表面特性に優れた熱間プレス用亜鉛めっき鋼板並びにこれを利用した熱間プレス成形部品及びその製造方法 - Google Patents
表面特性に優れた熱間プレス用亜鉛めっき鋼板並びにこれを利用した熱間プレス成形部品及びその製造方法 Download PDFInfo
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- 229910001335 Galvanized steel Inorganic materials 0.000 title claims description 40
- 239000008397 galvanized steel Substances 0.000 title claims description 40
- 238000004519 manufacturing process Methods 0.000 title claims description 31
- 229910000831 Steel Inorganic materials 0.000 claims description 137
- 239000010959 steel Substances 0.000 claims description 137
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- 238000005275 alloying Methods 0.000 claims description 27
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- 230000001590 oxidative effect Effects 0.000 claims description 6
- 229910052721 tungsten Inorganic materials 0.000 claims description 5
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- VASIZKWUTCETSD-UHFFFAOYSA-N manganese(II) oxide Inorganic materials [Mn]=O VASIZKWUTCETSD-UHFFFAOYSA-N 0.000 description 3
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- 150000004706 metal oxides Chemical class 0.000 description 2
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- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 229910007567 Zn-Ni Inorganic materials 0.000 description 1
- 229910007614 Zn—Ni Inorganic materials 0.000 description 1
- 239000002253 acid Substances 0.000 description 1
- 230000009471 action Effects 0.000 description 1
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- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
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- Oil, Petroleum & Natural Gas (AREA)
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- Coating With Molten Metal (AREA)
- Heat Treatment Of Articles (AREA)
- Shaping Metal By Deep-Drawing, Or The Like (AREA)
- Heat Treatment Of Sheet Steel (AREA)
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Description
以下、本発明の亜鉛めっき鋼板について詳しく説明する。
Cは、鋼板の強度を増加させる核心元素で、オーステナイト及びマルテンサイトの硬質相を生成させる。Cの含量が0.1%未満では、オーステナイト単相域で熱間プレスを行っても目標とする強度を確保することが困難であるため、Cの含量を0.1%以上添加することが好ましい。Cの含量が0.4%を超えると、靭性及び溶接性の低下が発生する可能性が高くなり、強度が高くなりすぎて焼鈍及びめっき工程で通板性を阻害するなど製造工程で不利な点があるため、Cの上限は0.4%以下に制限する。
Mnは固溶強化元素で、強度の上昇に大きく寄与するだけでなく、オーステナイトからフェライトへの変態を遅延させるのに重要な役割をする。Mnの含量が0.1%未満では、オーステナイトからフェライトへの変態温度(Ae3)が高くなり、鋼板をオーステナイト単相でプレス加工するためには、その分だけ高い熱処理温度が必要である。一方、Mnの含量が4.0%を超えると、溶接性、熱間圧延性などが劣化する恐れがあるため好ましくない。このとき、Mnによるフェライトへの変態温度(Ae3)の低減及び焼入性を十分に確保するためには、Mnの含量を0.5%以上とすることがより好ましい。
Siは脱酸の目的で添加される成分で、上記Siの含量が2%を超えると、熱延板の酸洗が困難で、熱延鋼板の未酸洗及び未酸洗酸化物によるスケール性表面欠陥を誘発することがある上、焼鈍時に鋼の表面にSiO2酸化物が生成され、未めっきが発生することがあるため、Siの上限は2%に限定することが好ましい。
Nは0.001%未満では、製鋼過程でNを制御するための製造費用が大きく上昇する恐れがあるため、その下限を0.001%とする。N含有量が0.02%を超えると、製造工程上、鋼板を溶解及び連鋳し難いため、製造費用が上昇することがあり、AlNによるスラブ亀裂が発生しやすい。よって、その上限を0.02%とする。
Bはオーステナイトからフェライトへの変態を遅延させる元素で、その含量が0.0001%未満では、その効果を十分に果たすことが困難で、Bの含量が0.01%を超えると、その効果が飽和するだけでなく、熱間加工性を低下させるため、その上限を0.01%に制限することが好ましい。
Ti、Nb及びVは鋼板の強度上昇、粒径微細化及び熱処理性を向上させるのに有効な元素である。上記含量が0.001%未満では、上記効果が十分に得られず、0.1%を超えると、製造費用の上昇及び炭窒化物が生成しすぎて、所望する強度及び降伏強度上昇の効果が期待できないため、上限を0.1%に限定することが好ましい。
CrとMoは硬化能を大きくするだけでなく、熱処理型鋼板の靭性を増加させるため、高い衝突エネルギー特徴が求められる鋼板に添加すると、その効果がさらに大きく、上記含量が0.001%未満では、上記の効果が十分に得られず、1.0%を超えると、その効果が飽和するだけでなく、製造費用が上昇するため、その上限を1.0%と制限することが好ましい。
Sbは熱間圧延時に粒界の選択酸化を抑制することで、スケールの生成を均一とし、熱間圧延材の酸洗性を向上させる役割をする元素である。Sb含量が0.001%未満では、その効果を果たすことが困難で、Sb含量が0.1%を超えると、その効果が飽和するだけでなく、製造費用が上昇して熱間加工時に脆性を起こすことがあるため、その上限を0.1%に制限することが好ましい。
Wは鋼板の熱処理硬化能を向上させる元素であると同時に、W含有析出物が強度確保に有利に作用する元素で、その含量が0.001%未満では、上記効果が十分に得られず、上記含量が0.3%を超えると、上記効果が飽和するだけでなく、製造費用の高くなるという問題点がある。よって、上記含量は0.001〜0.3%に制限することが好ましい。
以下、本発明の熱間プレス成形部品について詳しく説明する。
以下では、本発明の亜鉛めっき鋼板及び熱間プレス成形部品の製造方法について詳しく説明する。
まず、金属コーティング有無による焼鈍熱処理後の焼鈍酸化物の厚さを調べるために、重量%で、0.24C−0.04Si−2.3Mn−0.008P−0.0015S−0.025Alの組成を有する鋼板にNiコーティングをするか、しない後、785℃で焼鈍熱処理を行って亜鉛めっきを施してから素地鋼板内の金属表面拡散層上に形成される焼鈍酸化物の平均厚さを特定し、その結果を表1に示した。焼鈍酸化物の厚さはGOEDS分析とTEM断面分析により測定し、上記焼鈍酸化物の厚さは酸素の含量が10重量%まで落ちる地点までと判断し、めっき性を評価した。それから、上記溶融亜鉛めっき鋼板をHPF工程に適用した後、めっき層の保持有無を確認した。
表2に金属コーティング量、Zn層の初期厚さ、Zn浴中のAl濃度、合金化温度など素材の製造方法と、熱間プレス後のめっき層の厚さ、めっき層上に形成される酸化物の厚さ、めっき層のZn含量の構成比率を示した。めっき層のZn含量の比率はGOEDS分析時にめっき層のZnの構成比で示した。
まず、表3に記載された組成を有する鋼材を冷間圧延した鋼板を対象に実験した。
まず、表5に記載された組成を有する鋼材を冷間圧延した鋼板を対象に実験した。
まず、表9に記載された組成を有する鋼材を冷間圧延した鋼板を対象に実験した。
まず、表11に記載された組成を有する鋼材を冷間圧延した鋼板を対象に実験した。
Claims (14)
- 素地鋼板と、
前記素地鋼板上に形成された酸化反応時に酸素1モール当たりのギブス自由エネルギー減少量がCrより小さい金属が0.008重量%以上固溶されているFe−Zn相を含む亜鉛めっき層と、
前記亜鉛めっき層上に形成された平均厚さが0.01〜5μmである酸化物層とを含み、
前記酸化物層は、SiO 2 及びAl 2 O 3 からなる群より選択された1種以上の酸化物からなる平均厚さが10〜300nmである連続的な皮膜を含み、
前記連続的な皮膜上にZnO及びMnOを含む酸化物が形成され、
前記酸化反応時に酸素1モール当たりのギブス自由エネルギー減少量がCrより小さい金属は、Ni、Fe、Co、Cu、Sn、Sbからなる群より選択された1種以上である、
熱間プレス成形部品。 - 前記酸化物層はZnOを含み、MnO、SiO2及びAl2O3からなる群より選択された1種以上の酸化物を0.01〜50重量%含む請求項1に記載の熱間プレス成形部品。
- 前記連続的な皮膜上のZnO及びMnOを含む酸化物は重量%で比較してMnOの含量はZnOより小さい請求項1または2に記載の熱間プレス成形部品。
- 前記酸化物層は、FeOが10重量%以下である請求項1に記載の熱間プレス成形部品。
- 前記素地鋼板の上部に亜鉛拡散相が不連続的に存在する請求項1に記載の熱間プレス成形部品。
- 前記亜鉛拡散相の平均厚さが5μm以下である請求項5に記載の熱間プレス成形部品。
- 前記亜鉛めっき層のZn含量が30重量%以上である請求項1に記載の熱間プレス成形部品。
- 前記亜鉛めっき層の厚さは、熱間プレス成形前の厚さの1.5倍以上である請求項7に記載の熱間プレス成形部品。
- 前記亜鉛めっき層内のFe含量が60重量%以上である合金相の比率が、前記亜鉛めっき層全体に対して、70重量%以上である請求項1に記載の熱間プレス成形部品。
- 前記素地鋼板は、重量%で、C:0.1〜0.4%、Si:2.0%以下(0%は除外)、Mn:0.1〜4.0%、残部Fe及びその他不可避な不純物からなる請求項1から9の何れか1項に記載の熱間プレス成形部品。
- 前記素地鋼板は、重量%で、N:0.001〜0.02%、B:0.0001〜0.01%、Ti:0.001〜0.1%、Nb:0.001〜0.1%、V:0.001〜0.1%、Cr:0.001〜1.0%、Mo:0.001〜1.0%、Sb:0.001〜0.1%及びW:0.001〜0.3%からなる群より選択された1種以上をさらに含む請求項10に記載の熱間プレス成形部品。
- 鋼板に酸化反応時に酸素1モール当たりのギブス自由エネルギー減少量がCrより小さい金属をコーティングする段階と、
前記金属がコーティングされた鋼板を700〜900℃で焼鈍熱処理する段階と、
前記焼鈍熱処理された鋼板をAl:0.05〜0.5重量%、残部Zn及びその他不可避な不純物を含み、430〜500℃の温度範囲を有する溶融亜鉛めっき浴に浸漬して亜鉛めっきする段階と、
前記亜鉛めっきされた鋼板を酸化性雰囲気で、2〜10℃/秒の昇温速度で750〜950℃まで加熱した後、10分以下保持する段階と、
前記加熱後保持された鋼板を600〜900℃の温度範囲でプレス成形する段階とを含み、
前記酸化反応時に酸素1モール当たりのギブス自由エネルギー減少量がCrより小さい金属は、Ni、Fe、Co、Cu、Sn及びSbからなる群より選択された1種以上である、
熱間プレス成形部品の製造方法。 - 前記酸化反応時に酸素1モール当たりのギブス自由エネルギー減少量がCrより小さい金属をコーティングする段階は、前記金属を平均厚さ1〜1000nmでコーティングする請求項12に記載の熱間プレス成形部品の製造方法。
- 前記亜鉛めっきする段階後に600℃以下の温度範囲で合金化熱処理する段階をさらに含む請求項12または13に記載の熱間プレス成形部品の製造方法。
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JP2014221943A (ja) | 2014-11-27 |
US20150307977A1 (en) | 2015-10-29 |
CN102791901B (zh) | 2015-05-06 |
US9068255B2 (en) | 2015-06-30 |
WO2011081392A2 (ko) | 2011-07-07 |
CN104388870A (zh) | 2015-03-04 |
WO2011081392A9 (ko) | 2011-10-13 |
WO2011081392A3 (ko) | 2011-12-01 |
EP2520686A4 (en) | 2017-08-30 |
EP2520686A2 (en) | 2012-11-07 |
JP2013515863A (ja) | 2013-05-09 |
US11952652B2 (en) | 2024-04-09 |
US20120267012A1 (en) | 2012-10-25 |
US9945020B2 (en) | 2018-04-17 |
CN102791901A (zh) | 2012-11-21 |
ES2876258T3 (es) | 2021-11-12 |
JP5676642B2 (ja) | 2015-02-25 |
CN104388870B (zh) | 2017-04-12 |
WO2011081392A4 (ko) | 2012-01-19 |
EP2520686B1 (en) | 2021-04-07 |
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